WO2014126012A1 - Procédé pour la production d'acier martensitique - Google Patents

Procédé pour la production d'acier martensitique Download PDF

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WO2014126012A1
WO2014126012A1 PCT/JP2014/052884 JP2014052884W WO2014126012A1 WO 2014126012 A1 WO2014126012 A1 WO 2014126012A1 JP 2014052884 W JP2014052884 W JP 2014052884W WO 2014126012 A1 WO2014126012 A1 WO 2014126012A1
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treatment
sub
hours
zero
annealing
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勝彦 大石
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日立金属株式会社
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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
    • 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
    • C21D6/007—Heat treatment of ferrous alloys containing Co
    • 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
    • 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
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • 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
    • C22C38/005—Ferrous alloys, e.g. steel alloys containing rare earths, i.e. Sc, Y, Lanthanides
    • 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
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • 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
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • 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
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
    • 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
    • C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
    • 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
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
    • 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
    • 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
    • C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
    • 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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/008—Martensite

Definitions

  • the present invention relates to a method for producing martensitic steel.
  • Martensitic steel has excellent mechanical properties, high quenching hardness, and excellent wear resistance and fatigue strength. Therefore, steel for mechanical structures such as bearings, steel for knives such as knives and scissors, and for automobiles. It is used in a wide range of fields as sliding parts and aircraft parts. Conventionally, these materials have a plurality of manufacturing processes depending on the intended use and required steel ingot cleanliness.For example, when used as an aircraft member, a steel ingot having a predetermined component composition is obtained by vacuum melting. Manufactured and subjected to at least one remelting, for example, vacuum arc remelting (VAR) or electroslag remelting (ESR), followed by hot working or hot working and cold working. Yes.
  • VAR vacuum arc remelting
  • ESR electroslag remelting
  • the following heat treatment is performed during the manufacturing process or after adjusting to the final product shape.
  • softening and tempering treatment for the purpose of softening the material, solid solution treatment and quenching treatment to dissolve alloy elements in the material, and transformation of untransformed austenite remaining in the material after cooling treatment to martensite
  • a sub-zero treatment for softening for softening, a softening treatment for removing stress in the material caused by the martensitic transformation, and an aging treatment or tempering treatment for precipitating fine carbides and intermetallic compounds.
  • ⁇ -NiAl type intermetallic compound and M 2 C type carbide are precipitated in the aging treatment stage to form several percent reverse transformed austenite between lath martensite. To do. Thereby, it is possible to obtain martensitic steel excellent in strength and ductility.
  • the aging treatment is originally a treatment for precipitating the above-described carbides and intermetallic compounds in the material, and it is necessary to change the aging treatment temperature in order to adjust the amount of retained austenite by the aging treatment. When the aging treatment temperature changes, the shape and distribution of aging precipitates change while the distribution of reverse transformed austenite also changes, so it is very difficult to balance strength and ductility in production. was there.
  • An object of the present invention is to provide a method for producing martensitic steel for imparting ductility while maintaining the excellent strength characteristics of martensitic steel, that is, for achieving both strength and ductility.
  • the present invention (1) C: 0.18 to 0.30% by mass, Al: 1.0 to 2.0%, V: more than 0 and not more than 0.3%, Cr: 2.0 to 5.0%, Ni: 10.5 to 15.0% (where Ni ⁇ 7 + 3.5Al), Co: 5.0 to 7.0%, Mo alone or Mo + W / 2: 1.0 to 4.0%, selected element B, Si, Mn, Ca, rare earth element, Cu, Nb, B: 0 to 0.005%, Si: 0 to 0.4%, Mn: 0 to 0.4%, Ca: 0 to 0.05 %, Rare earth element: 0 to 0.05%, Cu: 0 to 1.0%, Nb: 0 to 0.10%, with the balance being Fe and impurities.
  • the sub-zero-treated material is subjected to age hardening for 5 to 20 hours in the temperature range of 475 to 600 ° C., or after low temperature aging treatment for 4 to 16 hours in the temperature range of 150 to 200 ° C.
  • the sub-zero treatment is a method for producing martensitic steel in which the temperature ranges from ⁇ 50 ° C. to 0 ° C.
  • the present invention also relates to a method for producing martensitic steel in which the volume fraction of retained austenite is 3.0-20.0% by the sub-zero treatment.
  • the annealing material may further contain Mg 0.0040% or less (excluding 0%) by mass%.
  • ductility can be imparted while maintaining the excellent strength characteristics of martensitic steel, that is, both strength and ductility can be achieved. Moreover, compared with the conventional process, the balance between strength and ductility is easy because the aging treatment necessary to obtain strength characteristics and the austenite phase amount necessary to obtain ductility can be adjusted in different processes. It is possible to adjust to.
  • the sub-zero treatment is a step performed after the preparation step of the annealing material, the annealing step, and the solution treatment step.
  • an age hardening process process is performed after a subzero process. The reasons for limiting these steps other than the sub-zero treatment step will be described later.
  • the sub-zero treatment is a solution treatment or a treatment for transforming the retained austenite present in the steel as untransformed austenite immediately after quenching to a stable martensite phase by cooling to room temperature or lower and soaking.
  • the present invention is based on the knowledge that the amount of retained austenite can be adjusted by adjusting the subzero treatment temperature.
  • Sub-zero treatment temperature range higher than ⁇ 50 ° C. and not higher than 0 ° C.
  • Residual austenite is a phase rich in ductility because the dough is softer than martensite. If such a phase can be left in the form of a film between the lath martensites, a martensitic structure rich in ductility is obtained.
  • the preferred range for the volume fraction of retained austenite is 3.0-20.0%. When the volume fraction of retained austenite is less than 3.0%, it becomes difficult to obtain the ductility imparting effect.
  • the volume fraction of retained austenite exceeds 20.0%, the austenite phase is not in the form of a film but in the form of a lump or block, and it is difficult to obtain the ductility imparting effect.
  • a more preferred lower limit of the volume fraction of retained austenite is 4.0%, and a more preferred upper limit of the volume fraction of retained austenite is 15.0%.
  • the subzero temperature for adjusting the amount of retained austenite is limited to a temperature range of ⁇ 50 ° C. or more and 0 ° C. or less.
  • the temperature range is ⁇ 50 ° C. or more and 0 ° C. or less.
  • the retained austenite phase in the steel can be made 3.0 to 20.0% by volume, so that the ductility imparting effect of the martensite phase can be expected.
  • a more preferable lower limit of the temperature range is ⁇ 40 ° C.
  • Subzero treatment time 0.5 to 5 hours
  • the subzero treatment time is set to 0.5 to 5 hours in the temperature range described above. This is because if the sub-zero treatment time is shorter than 0.5 hours, the retained austenite is insufficient to change to martensite. On the other hand, when the sub-zero treatment time is longer than 5 hours, the change of austenite to martensite reaches saturation. Therefore, when the sub-zero treatment time is set to a time exceeding 5 hours, there is a problem that not only a change in the metal structure cannot be expected, but it is difficult to maintain a constant temperature for a long time industrially. For the above reasons, the sub-zero treatment condition is a temperature range higher than ⁇ 50 ° C.
  • the treatment time is 0.5 to 5 hours.
  • the upper limit of the more preferable subzero treatment time is 3 hours or less.
  • C 0.18 to 0.30%
  • C is an element necessary for forming M 2 C carbides by combining with Cr, Mo, W, and V, and contributes to improvement of strength. If C is less than 0.18%, the amount of carbide that contributes to strength improvement cannot be obtained. On the other hand, when C exceeds 0.30%, austenite is stabilized, so that a large amount of retained austenite remains during quenching. Therefore, C is set to 0.18 to 0.30%.
  • Al 1.0-2.0%
  • Al is an element that precipitates as an intermetallic compound ⁇ -NiAl during aging treatment and contributes to strength improvement.
  • V More than 0 and 0.3% or less V is an element that stabilizes metastable M 2 C carbides and contributes to strength improvement. When V is 0%, M 2 C carbide cannot be present stably. On the other hand, if V exceeds 0.3%, the M 2 C stabilizing effect becomes excessive. Therefore, V exceeds 0 and is 0.3% or less. (If possible, I would like to set the lower limit of V. Also, the upper limit is also preferable. If other elements can also describe the preferable range, it should be described.)
  • Cr 2.0-5.0% Cr is an element that has the effect of stabilizing metastable M 2 C carbides. If Cr is less than 2.0%, the effect of stabilizing M 2 C cannot be obtained. On the other hand, when Cr exceeds 5.0%, M 23 C 6 is formed, and the carbide structure changes. Since the change in the carbide structure changes the strength characteristics, Cr is set to 2.0 to 5.0%.
  • Ni 10.5-15% (However, Ni ⁇ 7 + 3.5Al) Ni is an element that combines with Al to form ⁇ -NiAl, an intermetallic compound, contributes to improving the strength and also affects the transformation start temperature (Ms point) of martensite. Therefore, it is necessary to adjust Ni appropriately with respect to the amount of Al added.
  • Ni content is less than 10.5%, the ⁇ -NiAl content of the intermetallic compound decreases and the strength decreases.
  • Ni exceeds 15% the Ms point is significantly lowered, and a large amount of retained austenite is present during quenching. Therefore, Ni is made 10.5-15%.
  • the Ni content needs to satisfy Ni ⁇ 7 + 3.5Al.
  • Ni ⁇ 7 + 3.5Al is an index for obtaining an appropriate amount of an intermetallic compound necessary for maintaining high strength. If Ni is not 7 + 3.5Al or more, the amount of intermetallic compounds decreases, leading to a decrease in strength.
  • Co 5.0-7.0%
  • Co does not significantly affect the stability of the martensitic structure of the matrix and increases the solid solubility of aging precipitate-forming elements such as Mo and Al during the solution treatment, so that the solid solution of Mo and Al in the aging precipitation temperature range is increased. It is an important element contributing to aging precipitation strengthening by promoting precipitation of fine intermetallic compounds by lowering solubility. If Co is less than 5.0%, sufficient strength cannot be obtained. On the other hand, when Co exceeds 7.0%, austenite is stabilized and it becomes difficult to obtain a martensite structure. Therefore, Co is set to 5.0 to 7.0%.
  • Mo alone or Mo + W / 2 1.0 to 4.0%
  • Mo and W are elements that combine with C to form M 2 C carbides that contribute to strength improvement. If Mo alone or the total amount of Mo and W / 2 is less than 1.0%, carbide formation is insufficient. On the other hand, when Mo alone or the total amount of Mo and W / 2 exceeds 4.0%, a ⁇ phase (Fe 7 Mo 6 ) of an intermetallic compound is formed and forgeability is lowered. Therefore, the total amount of Mo alone or Mo + W / 2 is set to 1.0 to 4.0%.
  • the elements described above are essential elements of the present invention, and the balance is Fe and impurities.
  • any 1 or more types element of B, Si, Mn, Ca, rare earth elements, Cu, and Nb can be contained.
  • strength will fall when it exceeds the upper limit of each element shown below, if it adds selectively, it will limit to the following component range.
  • Mg: 0.0040% or less (0% is not included) can further be included by the mass%.
  • Mg: 0.0040% or less (excluding 0%) Mg is an element having specific properties that can improve ductility and toughness while maintaining the strength level of martensitic steel in the present invention.
  • ductility, toughness, and strength are contradictory properties, so that when one property is increased, the other property is lowered. Therefore, it has been very difficult to achieve both strength, ductility and toughness.
  • the mechanism by which ductility and toughness are improved by adding Mg has not been clarified at this stage, but is considered as follows.
  • the martensitic steel of the present invention is an alloy in which ⁇ -NiAl and M 2 C (M: Cr, Mo, V, etc.) carbides of intermetallic compounds are formed in the steel and the strength is increased by precipitation strengthening.
  • M M: Cr, Mo, V, etc.
  • Al contained in the alloy is easily combined with N in the steel to form nonmetallic inclusion AlN.
  • AlN is in a fine state, the degree of influence on the material properties is small, but if it is a coarse inclusion exceeding 10 ⁇ m, it becomes a starting point of fatigue failure and not only significantly reduces the strength but also causes a decrease in ductility.
  • Mg is considered to have the effect of suppressing the ductility deterioration due to AlN by being finely dispersed by becoming the core of AlN crystallization or precipitation during the melting and becoming the nucleus of AlN crystallization or precipitation.
  • impurity elements tend to diffuse and segregate to the grain boundaries in the hot working and heat treatment steps. When such segregation occurs, the grain boundary strength is impaired, and ductility cannot be obtained.
  • Mg when Mg is added, the impurity element forms precipitates with Mg, and the effect of suppressing segregation to the grain boundary, that is, It is considered that there is an effect of fixing the impurity element as a precipitate. It is considered that the grain boundary ductility is improved by such an effect.
  • Mg is not added, it is difficult to obtain the above-described effect.
  • Mg exceeds 0.0040%, a large amount of MgO is generated or coarsened, and functions as crystallization or precipitation nuclei as described above. May not be obtained, but may be combined with Al in the steel to form an Al—Mg-based oxide, resulting in a decrease in both strength and ductility. Therefore, Mg is made 0.0040% or less (excluding 0%).
  • a preferable upper limit of Mg is 0.0020%.
  • a preferable minimum is 0.0001%, More preferably, it is 0.0002%.
  • the lower limit for obtaining the above-mentioned Mg effect more reliably is 0.0010%.
  • the annealing material After preparing the aforementioned martensitic steel annealing material, the annealing material is annealed at a temperature range of 600 to 675 ° C. for 4 to 20 hours to obtain an annealed material.
  • the annealing treatment is intended to soften the martensitic steel.
  • the annealing temperature is less than 600 ° C., the martensitic steel is not sufficiently softened.
  • the annealing temperature exceeds 670 ° C., the constituent phase undergoes reverse transformation or austenite transformation, so that the material is hardened because it undergoes martensitic transformation by subsequent cooling.
  • the temperature range for annealing is set to 600 to 675 ° C.
  • the annealing time is less than 4 hours, the martensitic steel is not sufficiently softened and the annealing effect cannot be obtained.
  • the annealing time is 4 to 20 hours.
  • the above-mentioned annealed material is subjected to a solution treatment for at least 1 hour in a temperature range of 800 to 1000 ° C. to obtain a solution treatment material.
  • the solution treatment is intended to dissolve the alloy elements.
  • the temperature of the solution treatment is less than 800 ° C., the alloy elements are not sufficiently dissolved, and the effect of the solution treatment cannot be obtained.
  • the temperature of the solution treatment exceeds 1000 ° C., the prior austenite crystal grain size of the martensitic steel becomes coarse and causes a decrease in strength. Therefore, in the present invention, the temperature range of the solution treatment is set to 800 to 1000 ° C.
  • the solution treatment time is less than 1 hour, the alloy element is insufficiently dissolved, so that the solution treatment time is at least 1 hour.
  • the upper limit of the time of a solution treatment is not specifically limited, Even if it exceeds 10 hours, it becomes difficult to acquire the effect of the further solution treatment. Therefore, the upper limit of the solution treatment time may be 10 hours.
  • the sub-zero process is performed after the above-described solution treatment process. The reason for limiting the sub-zero process is as described above.
  • an age hardening treatment is performed on the sub-zero treatment material.
  • One of the following two conditions is selected as the age hardening treatment condition.
  • the first age hardening treatment condition (5 to 20 hours in a temperature range of 475 to 600 ° C.) will be described.
  • the age hardening treatment is intended to harden the base by depositing NiAl or M 2 C in the base (matrix).
  • the temperature of the aging treatment is less than 475 ° C., the time for age hardening becomes, for example, 50 hours or more, and the time is prolonged, and the productivity is remarkably lowered.
  • the temperature range of the first age hardening treatment is set to 475 to 600 ° C.
  • a preferred temperature range is 475 to 530 ° C.
  • the time of the age hardening treatment is less than 5 hours, the aging precipitation becomes insufficient, and the effect of the age hardening treatment cannot be obtained.
  • the age hardening treatment time exceeds 20 hours, it becomes an overaged state and causes a decrease in strength. Therefore, the first age hardening treatment time is set to 5 to 20 hours. A preferred time range is 5 to 15 hours.
  • the second age-hardening treatment condition is obtained by adding a low-temperature aging treatment for 5 to 20 hours in a temperature range of 150 to 200 ° C. before the first age-hardening treatment described above.
  • the low temperature aging treatment is a treatment for softening the martensite phase obtained in the solution treatment step to obtain strength and ductility.
  • the temperature of the low temperature aging treatment of the second age hardening treatment is less than 150 ° C.
  • the martensite phase is insufficiently softened and the effect of the low temperature aging treatment cannot be obtained.
  • the temperature range of the low temperature aging treatment of the second age hardening treatment is set to 150 to 200 ° C.
  • the time of the low temperature aging treatment of the second age hardening treatment is less than 4 hours, the martensite phase is insufficiently softened and the effect of the low temperature aging treatment cannot be obtained.
  • the low-temperature aging treatment time of the second age hardening treatment is set to 4 to 16 hours.
  • the reason for the limitation for 5 to 20 hours in the temperature range of 475 to 600 ° C. performed following the low temperature aging treatment conditions described above is the same as the first age hardening treatment conditions described above.
  • the amount of retained austenite is adjusted by optimizing the sub-zero treatment, but the retained austenite remaining at the time of sub-zero changes with time to martensite.
  • the alloy elements diffuse into the residual austenite remaining at the sub-zero time, and as a result, the austenite phase is solid-solution strengthened, so that a stable retained austenite structure can be obtained.
  • This effect is the same effect obtained by selecting any of the above-mentioned two conditions of age hardening treatment, but when the second age hardening treatment is applied, non-uniform distortion caused by heat treatment or processing can be removed.
  • the effect of making the precipitation distribution of intermetallic compounds etc. more uniform can be expected.
  • the selection of the two age-hardening treatments may be performed by selecting the first age-hardening treatment, for example, when productivity is important.
  • Example 1 A 10 kg ingot of martensitic steel shown in Table 1 was produced by a vacuum induction melting furnace, and a bar having a cross-sectional shape of 30 mm ⁇ 30 mm was obtained through homogenization annealing and hot forging. Thereafter, normalization was performed at 870 ° C. for 1 hour in the air to obtain a material for annealing.
  • An annealing material was obtained by annealing at 650 ° C. ⁇ 8 h using the annealing material described above, and then a solid solution treatment was performed at 900 ° C. ⁇ 1 h using the annealing material to obtain a solid solution treatment material.
  • a sub-zero treatment is carried out for 2 hours in an ethyl alcohol solution adjusted to a sub-zero temperature of ⁇ 78 ° C., a temperature of ⁇ 37 ° C. and a temperature of ⁇ 12 ° C. according to the present invention.
  • a low temperature aging treatment of 200 ° C. ⁇ 8 h and a second age hardening treatment of 495 ° C. ⁇ 10 h were further performed.
  • test pieces were cut out from the martensitic steel bar subjected to age hardening treatment, and the amount of retained austenite was measured, a tensile test, and a Charpy impact test were performed.
  • the amount of retained austenite is measured by cutting a 10 mm ⁇ 10 mm ⁇ 5 mm size test piece from a martensitic steel bar, mechanically polishing the surface of the test piece, removing the residual stress on the surface by electrolytic polishing, Measured by peak intensity comparison.
  • a block material of an arbitrary size was cut out from a martensitic steel bar and processed into a tensile test piece shape having a parallel part length of 32 mm, a parallel part diameter of 6.35 mm, a test piece total length of 90 mm, and a grip part diameter of 10 mm. Thereafter, it was performed according to ASTM-E8.
  • the Charpy impact test was carried out in accordance with JIS-Z2242, by cutting out a block material of an arbitrary size from a martensitic steel bar and applying a V-notch process of 10 mm ⁇ 10 mm ⁇ 5 mm and 2 mm in depth.
  • the tensile test and Charpy impact test were performed at room temperature. Table 2 shows the measurement and test results.
  • Example 2 A 10 kg ingot of martensitic steel shown in Table 3 was produced by a vacuum induction melting furnace, and a bar having a cross-sectional shape of 30 mm ⁇ 30 mm was obtained through homogenization annealing and hot forging. Thereafter, normalization was performed at 870 ° C. for 1 hour in the air to obtain a material for annealing. An annealing material was obtained by annealing at 650 ° C. ⁇ 8 h using the above-described annealing material, and then a solid solution treatment was performed at 900 ° C. ⁇ 1 h using the annealing material.
  • a sub-zero treatment material was obtained by carrying out a sub-zero treatment for 2 hours in an ethyl alcohol solution adjusted to a sub-zero temperature of ⁇ 12 ° C. of the present invention, and then 200 ° C. ⁇ 8 h.
  • Low temperature aging treatment and a second age hardening treatment of 495 ° C. ⁇ 10 h.
  • test pieces were cut out from the martensitic steel bar subjected to age hardening treatment, and the amount of retained austenite was measured, a tensile test, and a Charpy impact test were performed.
  • the amount of retained austenite is measured by cutting out a 10 mm ⁇ 10 mm ⁇ 5 mm size test piece from a martensite steel bar, mechanically polishing the surface of the test piece, removing the residual stress on the surface by electrolytic polishing, and using an X-ray diffraction method. Measured.
  • the amount of retained austenite was measured using a Rigaku X-ray diffractometer (RINT200) under the conditions of a Co source, a voltage of 40 kV, and a current of 200 mA (110) ⁇ , (200) ⁇ , (211) ⁇ , (200) ⁇ , (220) ⁇ , and (311) ⁇ were calculated using the diffraction line intensity ratio obtained from each surface.
  • RINT200 Rigaku X-ray diffractometer
  • a block material of an arbitrary size was cut out from a martensitic steel bar and processed into a tensile test piece shape having a parallel part length of 32 mm, a parallel part diameter of 6.35 mm, a test piece total length of 90 mm, and a grip part diameter of 10 mm. Thereafter, it was performed according to ASTM-E8.
  • the Charpy impact test was carried out in accordance with JIS-Z2242, by cutting out a block material of an arbitrary size from a martensitic steel bar and applying a V-notch process of 10 mm ⁇ 10 mm ⁇ 5 mm and 2 mm in depth.
  • the tensile test and Charpy impact test were performed at room temperature. Table 4 shows the measurement and test results.
  • the No. of the present invention added with Mg. Nos. 4 and 5 have the same tensile strength as that of the conventional example shown in Table 2, but the tensile test elongation, drawing and Charpy impact values are increased, indicating that the ductility is improved. Further, No. 1 of the present invention to which Mg was added. Nos. 4 and 5 are the same as No. 1 of the present invention. Compared with 2 and 3, the Charpy impact value is slightly inferior, but it can be confirmed that the elongation and aperture value are high and the ductility is improved.
  • the metal structure of the test piece was a martensite structure except for the retained austenite ( ⁇ R ) in the amount shown in Table 4 except for precipitates such as carbides.

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Abstract

L'invention porte sur un procédé pour la production d'acier martensitique qui lui confère de la ductilité tout en conservant ses excellentes propriétés de résistance, ou en d'autres termes, qui équilibre la ductilité et la résistance. Ce procédé pour la production d'acier martensitique comprend la préparation d'un matériau de recuit ayant une composition qui contient, en % en masse, du C à hauteur de 0,18-0,30 %, de l'Al à hauteur de 1-2 %, du V à hauteur de plus de 0 et pas plus de 0,3 %, du Cr à hauteur de 2-5 %, du Ni à hauteur de 10,5-15 %, Ni étant ≥ 7 + 3,5 Al, du Co à hauteur de 5-7 % et du Mo seul ou Mo + W/2 à hauteur de 1-4 % ; et qui contient des éléments choisis constitués de B, Si, Mn, Ca, des éléments terres rares, Cu et Nb, B représentant 0-50 ppm, Si représentant 0-0,4 %, Mn représentant 0-0,4 %, Ca représentant 0-500 ppm, les éléments terres rares représentant 0-500 ppm, Cu représentant 0-1 % et Nb représentant 0-0,1 %, le reste étant constitué de Fe et d'impuretés. Ce procédé pour la production d'acier martensitique comprend également une étape de recuit, de mise en œuvre d'un traitement en solution, de mise en œuvre d'un traitement par le froid et de mise en œuvre d'un traitement de durcissement par vieillissement. Dans celui-ci, le traitement par le froid est effectué pendant 0,5 à 5 heures sur une plage de température supérieure à -50°C et inférieure ou égale à 0°C.
PCT/JP2014/052884 2013-02-12 2014-02-07 Procédé pour la production d'acier martensitique WO2014126012A1 (fr)

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JP2008539331A (ja) * 2005-04-27 2008-11-13 オウベル・アンド・デュヴァル 焼戻しマルテンサイト鋼、該鋼からの部品の製造方法、及びそのように得られた部品
JP2012531525A (ja) * 2009-07-03 2012-12-10 スネクマ 混合硬化でのマルテンサイト系鋼の低温処理

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* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2008539331A (ja) * 2005-04-27 2008-11-13 オウベル・アンド・デュヴァル 焼戻しマルテンサイト鋼、該鋼からの部品の製造方法、及びそのように得られた部品
JP2012531525A (ja) * 2009-07-03 2012-12-10 スネクマ 混合硬化でのマルテンサイト系鋼の低温処理

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