EP2537952B1 - Produit coulé en acier inoxydable de décolletage et procédé de fabrication - Google Patents

Produit coulé en acier inoxydable de décolletage et procédé de fabrication Download PDF

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Publication number
EP2537952B1
EP2537952B1 EP11812136.7A EP11812136A EP2537952B1 EP 2537952 B1 EP2537952 B1 EP 2537952B1 EP 11812136 A EP11812136 A EP 11812136A EP 2537952 B1 EP2537952 B1 EP 2537952B1
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Prior art keywords
stainless steel
particles
cast
cast product
added
Prior art date
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EP11812136.7A
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German (de)
English (en)
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EP2537952A4 (fr
EP2537952A1 (fr
Inventor
Satoshi Emura
Shigeo Yamamoto
Kazuyuki Sakuraya
Kaneaki Tsuzaki
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National Institute for Materials Science
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National Institute for Materials Science
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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
    • C21D6/002—Heat treatment of ferrous alloys containing Cr
    • 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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • 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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/56—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering characterised by the quenching agents
    • C21D1/60—Aqueous agents
    • 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
    • C21D5/00—Heat treatments of cast-iron
    • 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
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C1/00—Making non-ferrous alloys
    • C22C1/02—Making non-ferrous alloys by melting
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C33/00—Making ferrous alloys
    • C22C33/04—Making ferrous alloys by melting
    • 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
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • 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
    • C21D2211/004—Dispersions; Precipitations

Definitions

  • the present invention relates to methods of production of a stainless steel cast product to which a free-cutting additive has been added.
  • a stainless steel cast product to which corrosion resistance is important for example, pipe couplings (e.g. elbows, sockets, and nipples) used in plumbing, vacuum equipments and analytical equipments, valves, and flanges for coupling, is produced by casting.
  • Pipe couplings e.g. elbows, sockets, and nipples
  • machining cutting work
  • These products are required to have excellent corrosion resistance, and therefore austenitic stainless steel, such as SUS 304, and SUS 316, is often used.
  • austenitic stainless steel is prone to work hardening.
  • the austenitic stainless steel is therefore known to have poor machinability, due to work hardening occurred adjacent to the cutting surface.
  • the sulfur-added free-cutting stainless steel can be used only in a low corrosiveness environment, or for products that do not require corrosion resistance. From these reasons, a free-cutting stainless steel cast product, which ensures both excellent machinability and corrosion resistance, has not yet been provided to date.
  • PTL 1 discloses free-cutting stainless steel ensuring excellent machinability, corrosion resistance, and mechanical properties at the same time, and a production method thereof.
  • this invention improved machinability of the free-cutting stainless steel by about 25% compared to a conventional stainless steel material, by performing forging and rolling on an ingot after casting to eliminate a cast structure, and re-precipitating hexagonal boron nitride (h-BN) particles.
  • h-BN hexagonal boron nitride
  • the present invention aims to provide methods of production of a free-cutting stainless steel cast product, which can ensure all of the excellent machinability, environmental friendliness, and corrosion resistance, as a cast steel product that does not require mechanical properties so much, but requires machinability for giving complicated shapes, and to provide a production method thereof.
  • the present invention provides a method of production of a stainless steel product according to claim 1.
  • the present invention provides a method of production of a stainless steel product according to claim 2. Further features of the invention are defined in the dependent claims.
  • the present invention is accomplished based on the insight that a method of production of a stainless steel cast product having excellent machinability and corrosion resistance can be provided by effectively utilizing characteristics of hexagonal boron nitride (h-BN) particles that are excellent as a solid lubricant, chemically stable, and not damaged by either acid or alkali, and by utilizing precipitation, or solid solution/re-precipitation of h-BN by performing a particular heat treatment even in the state of the cast structure.
  • h-BN hexagonal boron nitride
  • the stainless steel cast product contains a free-cutting additive, which is hexagonal boron nitride (h-BN) particles, in which the h-BN particles have particle diameters of 200 nm to 10 ⁇ m, are spherical particles, and are uniformly dispersed and precipitated in steel.
  • h-BN hexagonal boron nitride
  • the production method is directed to cooling molten stainless steel at a cooling rate by which h-BN particles are precipitated in a temperature range of 1,250°C to 850°C during casting solidification, to thereby disperse and precipitate the h-BN particles therein.
  • a production method of the stainless steel cast product contains: heating cast stainless steel, in a cast structure of which h-BN particles are unevenly precipitated, to temperature equal to or higher than 1,200°C, followed by quenching the cast stainless steel at a cooling rate by which the h-BN particles are not precipitated, to turn into a state of a solid solution, whereby eliminating the h-BN particles; and tempering the cast stainless steel at a temperature ranging from 950°C to 1,100°C to again disperse and precipitate h-BN particles.
  • a production method of the stainless steel cast product comprises: quenching molten stainless steel at a cooling rate by which h-BN particles are not precipitated, in a temperature range of 1,250°C to 850°C during casting solidification, to give a cast structure where no h-BN particle is precipitated; and tempering the cast stainless steel at temperature ranging from 950°C to 1,100°C to disperse and precipitate h-BN particles therein.
  • the boron (B) is added into the molten stainless steel in an amount of 0.003% by mass to 0.5% by mass
  • the nitrogen (N) is added into the molten stainless steel in an amount that a molar ratio of N/B becomes 1 or more.
  • the B is added to the molten stainless steel in the form of ferroboron or metallic boron
  • the N is added to the molten stainless steel by providing a mixed gas of argon and nitrogen (argon + nitrogen) or reduced-pressure nitrogen as a melting atmosphere for the molten stainless steel.
  • the B is added to the molten stainless steel in the form of ferroboron or metallic boron
  • the N is added to the molten stainless steel in the form of a compound or ferroalloy containing nitrogen.
  • the methods of the invention provided for a stainless steel cast product whose machinability is improved without deteriorating of corrosion resistance as a result of uniformly dispersing and precipitating h-BN particles as excellent solid lubricants, which are chemically stable and are not damaged by either acid or alkali, as well as provided a production method thereof.
  • the stainless steel cast product can ensure not only excellent machinability and environmental friendliness, but also corrosion resistance.
  • h-BN particles having excellent properties as a solid lubricant for cast stainless steel.
  • This application of the h-BN particles makes it possible to realize a stainless steel cast product, which ensures not only machinability, but also environmental friendliness as environmentally hazardous elements, e.g., Pb and Se, are not used, and inhibits deterioration of corrosion resistance.
  • the present invention has characteristics as described above, and embodiments thereof will be explained hereinafter.
  • melting of cast stainless steel is performed by means of a melting furnace, which is capable of adjusting melting atmosphere, and is generally used for melting of stainless steel.
  • a melting furnace which is capable of adjusting melting atmosphere, and is generally used for melting of stainless steel.
  • ferroboron or metallic boron is used as a source of B, but use of the ferroboron having a low melting point is technically advantageous, and is economical as a cost per unit weight of B is low.
  • the B content is determined as the final B content in the stainless steel cast product, which is preferably 0.003% by mass to 0.5% by mass, more preferably 0.01% by mass to 0.2% by mass.
  • a method for adding N there are a method where the molten stainless steel is allowed to absorb N in a melting atmosphere, and a method in which nitride of alloying elements constituting stainless steel, such as chromium nitride, and ferrochromium nitride, is added to the molten stainless steel.
  • nitride of alloying elements constituting stainless steel such as chromium nitride, and ferrochromium nitride
  • the N content in the stainless steel cast product may be an amount that a molar ratio of N/B becomes 1 or more, for a general standard.
  • the molar ratio of N/B in the cast stainless steel is smaller than 1, an amount of the solute B increases, which reduces an amount of precipitated h-BN particles that are useful for machinability. Accordingly, it is desired that the molar ratio of N/B is as large as possible.
  • the N content varies depending on chemical compositions of the cast stainless steel, but as B increases, an equivalent N concentration decreases in the steel, because B increases the activity of N. In the chemical composition of SUS 304 stainless steel, the N content is 0.25% by mass or lower, exclusive of melting under pressurized nitrogen atmosphere.
  • the molten stainless steel containing B and N, prepared in the aforementioned manner can precipitate and distribute h-BN spherical particles having particle diameter of 200 nm to 10 ⁇ m in the cast structure, by controlling a cooling rate thereof in the precipitation temperature range of h-BN, i.e., 1,250°C to 850°C, during the solidification in a mold.
  • h-BN coarsely grown to the size of about 20 ⁇ m to about 30 ⁇ m may be unevenly distributed and precipitated in a portion of the product, depending on a cooling rate in a cooling process after casting.
  • a cooling rate in a cooling process after casting To avoid uneven distribution and precipitation of coarse h-BN particles:
  • the h-BN precipitated in the stainless steel cast product is decomposed into B and N and is turned into a solid solution in a matrix of the cast stainless steel by being held at the temperature of 1,200°C or higher, for a relatively short time (e.g., 0.5 hours to 1 hour, at 1,250°C). Note that, such treatment is not possible when the stainless steel cast product is melted, and therefore it is necessary to perform the treatment at temperature lower than the melting point of the steel.
  • An operation for quenching may be water quenching, which is generally performed for stainless steel, but the cooling rate in the below-mentioned temperature range at which h-BN is precipitated needs to be adjusted to a cooling rate at which precipitation does not occur.
  • the supersaturated B and N are re-precipitated as h-BN during tempering at the temperature of 800°C to 1,150°C.
  • nucleation of h-BN is prioritized rather than growth because of the following two factors, that are a difference between equilibrium solubility and supersaturation solubility of B and N is large at this temperature, and diffusion lengths of B and N are small because diffusion velocities of B and N are slow at this temperature. Therefore, very finely and uniformly precipitated h-BN appears in the entire material.
  • coarsely grown h-BN precipitates appear as growth of h-BN is prioritized rather than nucleation.
  • the tempering temperature at which the particle diameters and distribution suited for giving excellent machinability is in the range of 950°C to 1,100°C.
  • the tempering period As for the tempering period, the higher the tempering temperature is the shorter the period is, as diffusion velocities of B and N are fast as the temperature is high.
  • the period is therefore in the range of 0.5 hours to 3 hours, preferably 1 hour to 2 hours.
  • quenching is performed after the tempering.
  • a commercial austenitic stainless steel (SUS 304) round bar (weight: 18 kg) was used as a melting raw material, and was melted by means of a vacuum induction melting furnace.
  • a chemical composition (% by mass) of the melting raw material included 0.04% of C, 0.30% of Si, 1.00% of Mn, 0.030% of P, 0.024% of S, 8.09% of Ni, and 18.05% of Cr.
  • N gas with partial pressure of 0.07 MPa was introduced in the vacuum induction melting furnace, to adjust a concentration of N in the molten steel.
  • a predetermined amount of commercial ferroboron (19.2% by mass of B) was added to the molten steel to adjust a concentration of B.
  • the resultant was maintained in a reduced-pressure nitrogen atmosphere for 20 minutes, and cast at 1,600°C into a cast iron mold, to thereby produce an ingot.
  • the target values of the B contents of Developed Materials 1 to 3 were respectively 0.02% by mass, 0.05% by mass, and 0.1% by mass, and the target values of the N contents thereof were 0.2% by mass, respectively.
  • Comparative Material 1 was produced (corresponding to SUS 304 cast stainless steel without h-BN) in the same melting and casting conditions to produce an ingot in the manner as in Developed Materials 1 to 3, provided that the melting raw material was melted in an Ar atmosphere.
  • Comparative Material 2 a material in which 0.3% by mass of S was added to Comparative Material 1 (corresponding to SUS303 cast stainless steel, sulfur-added free-cutting cast stainless steel) was produced.
  • Comparative Material 3 a material in which, similarly to Developed Materials 1 to 3, 0.2% by mass of N was added to Comparative Material 1 was produced.
  • an h-BN solution treatment was performed, which was the heat treatment in an electric resistance heating furnace in air for 0.5 hours at 1,250°C followed by water quenching outside the furnace.
  • an h-BN precipitation treatment was performed, which was the heat treatment in an electric resistance heating furnace in air for 1 hour at 1,050°C followed by water quenching outside the furnace.
  • this heat treatment was performed on the developed materials and comparative materials under the same conditions.
  • FIGs. 1 to 3 are SEM (scanning electron microscopy) micrographs depicting precipitation and dispersion states of the precipitates in Developed Material 1, Developed Material 3, and Comparative Material 2, respectively.
  • a round bar having a diameter of 3.6 mm was cut from the heat treated sample, circumferentially notched, and bent at the notched position, and the fracture surface of the bent bar was observed by SEM.
  • the SEM was equipped with an energy dispersive X-ray spectroscopy (EDS), and elementary analysis of nonmetallic inclusions observed on the fracture surface was performed by the EDS, to thereby determine the nonmetallic inclusions.
  • EDS energy dispersive X-ray spectroscopy
  • FIG. 1 it was observed that some h-BN particles (indicated by solid arrows) having the size of 10 ⁇ m or smaller were dispersed at the bottom of dimples over the entire fracture surface in the visual field with the magnification of ⁇ 200. Also, some spherical MnS particles (indicated by dashed arrows) having the size of about 10 ⁇ m derived from a trace of sulfur and manganese contained in the melting raw material were observed.
  • FIG. 2 similarly to FIG. 1 , it was observed that the h-BN particles having the size of 10 ⁇ m or smaller were dispersed in the entire fracture surface in the visual field with the magnification of ⁇ 200.
  • the number of the h-BN particles was approximately 10 times the number thereof of Developed Material 1, with proportional to the concentration of B. It was assumed from the shapes of the h-BN particles observed in FIGs. 1 and 2 that supersaturated B and N in the molten steel were precipitated as the h-BN particles in the solidification process of the molten steel.
  • MnS spherical particles having the size of about 10 ⁇ m to about 30 ⁇ m was observed at the bottom of dimples over the entire fracture surface in the visual field with the magnification of ⁇ 200. These MnS particles were also observed in FIG. 1 , and were assumed from their particle diameters and shapes to be crystallized when the steel was in the molten state.
  • FIG. 4 depicts an effect of the h-BN particles or MnS particles dispersed in the material on the machinability.
  • the conditions for the turning test included the cutting depth of 1.0 mm, the feed rate of 0.1 mm/rev, and the tool material of M30 (without chip breaker), no use of cutting oil, and the turning cutting speed of 12 m/min to 200 m/min. Under these conditions, the measurement values were obtained.
  • Developed Material 4 reduced the combined cutting force by 20% in the intermediate cutting speed region, 11% in the high cutting speed region, compared to Comparative Material 1 (corresponding to SUS 304 cast stainless steel), and the machinability thereof was significantly improved.
  • Comparative Material 2 was sulfur-added free-cutting cast stainless steel, and the machinability of the developed materials was lower than that of Comparative Material 2. In the case where corrosion resistance of a cast steel product is important, however, Comparative Material 2 cannot be used. Only the developed materials can ensure both excellent machinability and corrosion resistance, the superiority of the developed materials over the comparative materials cannot be denied.
  • FIG. 5 depicts a relationship between cutting speed and combined cutting force of the samples of Developed Materials 1 to 3, where the amount of B added was varied, and Comparative Material 3 (B was not added) in the turning process. As presented in Table 1, these four materials had substantially the same level of the N content, which was about 0.2% by mass.
  • FIG. 5 depicts an effect of the addition of B on the machinability. Compared to Comparative Material 3 whose concentration of B was 0% by mass, it was observed that the developed materials to which B was added reduced the cutting resistance in almost all regions of the cutting speed, and therefore it was confirmed that the machinability was improved by addition of B.
  • FIG. 6 depicts the results of the corrosion test performed in accordance with the method of sulfuric acid test for stainless steel (JIS G 0591). The conditions for the test were as follows. Each sample was immersed in boiled 5%H 2 SO 4 for 6 hours consecutively. The value obtained by dividing the corrosion weight loss with the initial surface area of the sample was determined as a corrosion amount. The obtained corrosion amounts were compared.
  • the present invention can easily provide a stainless steel cast product, which is environmentally friendly and has improved its machinability without deteriorating its corrosion resistance, and hence the present invention can provide excellent utility of the stainless steel cast product in various processing fields.

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

Claims (5)

  1. Un procédé de fabrication d'un produit coulé en acier inoxydable, consistant à :
    chauffer l'acier inoxydable coulé, dans une structure coulée dont les particules de h-BN sont précipitées irrégulièrement, à une température égale ou supérieure à 1200°C, suivi par une trempe de l'acier inoxydable coulé à une vitesse de refroidissement grâce à laquelle les particules de h-BN ne sont pas précipitées, pour passer à un état de solution solide, ce qui élimine ainsi les particules de h-BN ; et
    effectuer un revenu de l'acier inoxydable coulé dans une plage de températures comprise entre 950°C et 1100°C pour de nouveau disperser et précipiter les particules de h-BN,
    dans lequel le produit coulé en acier inoxydable comprend :
    un additif de décolletage, qui est composé de particules hexagonales de nitrure de bore (h-BN),
    dans lequel les particules de h-BN ont un diamètre de particule compris entre 200 nm et 10 µm, sont des particules sphériques et sont dispersées et précipitées uniformément dans le produit coulé en acier inoxydable.
  2. Un procédé de fabrication d'un produit coulé en acier inoxydable, consistant à :
    effectuer une trempe de l'acier inoxydable en fusion à une vitesse de refroidissement grâce à laquelle les particules de h-BN ne sont pas précipitées dans une plage de températures comprise entre 1250°C et 850°C pendant la solidification du produit moulé, pour donner une structure coulée où aucune particule de h-BN n'est précipitée ; et
    effectuer un revenu de l'acier inoxydable coulé dans une plage de températures comprise entre 950°C et 1100°C afin de disperser et de précipiter les particules de h-BN dans celui-ci,
    dans lequel le produit coulé en acier inoxydable comprend :
    un additif de décolletage, qui est composé de particules hexagonales de nitrure de bore (h-BN),
    dans lequel les particules de h-BN ont un diamètre de particule compris entre 200 nm et 10 µm, sont des particules sphériques et sont dispersées et précipitées uniformément dans le produit coulé en acier inoxydable.
  3. Le procédé de fabrication du produit coulé en acier inoxydable selon la revendication 1 ou 2, dans lequel le bore (B) est ajouté à l'acier inoxydable en fusion dans une quantité comprise entre 0,003% et 0,5% en masse, et l'azote (N) est ajouté à l'acier inoxydable en fusion dans une quantité telle que le rapport molaire de N / B devient 1 ou plus.
  4. Le procédé de fabrication du produit coulé en acier inoxydable selon la revendication 3, dans lequel le B est ajouté to l'acier inoxydable en fusion sous la forme de ferrobore ou de bore métallique, et le N est ajouté à l'acier inoxydable en fusion en fournissant un gaz mélangé composé d'argon et d'azote (argon + azote) ou d'un azote à pression réduite comme étant une atmosphère de fusion pour l'acier inoxydable en fusion.
  5. Le procédé de fabrication du produit coulé en acier inoxydable selon la revendication 3, dans lequel le B est ajouté à l'acier inoxydable en fusion sous la forme de ferrobore ou de bore métallique, et le N est ajouté à l'acier inoxydable en fusion sous la forme d'un composé ou d'un ferro-alliage contenant de l'azote.
EP11812136.7A 2010-07-27 2011-04-22 Produit coulé en acier inoxydable de décolletage et procédé de fabrication Not-in-force EP2537952B1 (fr)

Applications Claiming Priority (2)

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JP2010167872 2010-07-27
PCT/JP2011/059910 WO2012014541A1 (fr) 2010-07-27 2011-04-22 Produit coulé en acier inoxydable de décolletage et procédé de fabrication

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EP2537952A1 EP2537952A1 (fr) 2012-12-26
EP2537952A4 EP2537952A4 (fr) 2014-05-07
EP2537952B1 true EP2537952B1 (fr) 2016-12-28

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JP (1) JP5713299B2 (fr)
CN (1) CN102959111B (fr)
WO (1) WO2012014541A1 (fr)

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JP6103746B2 (ja) * 2012-08-23 2017-03-29 国立研究開発法人物質・材料研究機構 快削鉄系形状記憶合金
CN104513143A (zh) 2013-09-26 2015-04-15 陶氏技术投资有限责任公司 加氢甲酰化方法
CN105331779A (zh) * 2015-11-20 2016-02-17 沈阳黎明航空发动机(集团)有限责任公司 一种减少1Cr13钢制零件氮化起泡的工艺方法
JP2024513740A (ja) 2021-03-31 2024-03-27 ダウ テクノロジー インベストメンツ リミティド ライアビリティー カンパニー ヒドロホルミル化プロセス

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EP2048257B1 (fr) * 2006-07-31 2014-02-19 National Institute for Materials Science Acier inoxydable de decoupe libre et son procédé de fabrication
JP6044037B2 (ja) * 2010-04-30 2016-12-14 国立研究開発法人物質・材料研究機構 精密加工用快削ステンレス鋼素材及びその製造方法

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JPWO2012014541A1 (ja) 2013-09-12
CN102959111B (zh) 2017-07-04
JP5713299B2 (ja) 2015-05-07

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