WO2011135897A1 - 精密加工用快削ステンレス鋼素材及びその製造方法 - Google Patents

精密加工用快削ステンレス鋼素材及びその製造方法 Download PDF

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WO2011135897A1
WO2011135897A1 PCT/JP2011/053330 JP2011053330W WO2011135897A1 WO 2011135897 A1 WO2011135897 A1 WO 2011135897A1 JP 2011053330 W JP2011053330 W JP 2011053330W WO 2011135897 A1 WO2011135897 A1 WO 2011135897A1
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Prior art keywords
stainless steel
cutting
free
steel material
precision machining
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PCT/JP2011/053330
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English (en)
French (fr)
Japanese (ja)
Inventor
聡 江村
重男 山本
和之 櫻谷
津崎　兼彰
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独立行政法人物質・材料研究機構
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Priority to EP11774682.6A priority Critical patent/EP2565286A4/en
Priority to CN201180021615.7A priority patent/CN102906290B/zh
Publication of WO2011135897A1 publication Critical patent/WO2011135897A1/ja

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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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/0068—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for particular articles not mentioned below
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21C—PROCESSING OF PIG-IRON, e.g. REFINING, MANUFACTURE OF WROUGHT-IRON OR STEEL; TREATMENT IN MOLTEN STATE OF FERROUS ALLOYS
    • C21C5/00—Manufacture of carbon-steel, e.g. plain mild steel, medium carbon steel or cast steel or stainless steel
    • C21C5/005—Manufacture of stainless steel
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21C—PROCESSING OF PIG-IRON, e.g. REFINING, MANUFACTURE OF WROUGHT-IRON OR STEEL; TREATMENT IN MOLTEN STATE OF FERROUS ALLOYS
    • C21C7/00—Treating molten ferrous alloys, e.g. steel, not covered by groups C21C1/00 - C21C5/00
    • C21C7/0006—Adding metallic additives
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21C—PROCESSING OF PIG-IRON, e.g. REFINING, MANUFACTURE OF WROUGHT-IRON OR STEEL; TREATMENT IN MOLTEN STATE OF FERROUS ALLOYS
    • C21C7/00—Treating molten ferrous alloys, e.g. steel, not covered by groups C21C1/00 - C21C5/00
    • C21C7/04—Removing impurities by adding a treating agent
    • C21C7/072—Treatment with gases
    • 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
    • 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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • 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
    • C22C38/002—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
    • C22C38/02—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
    • C21C—PROCESSING OF PIG-IRON, e.g. REFINING, MANUFACTURE OF WROUGHT-IRON OR STEEL; TREATMENT IN MOLTEN STATE OF FERROUS ALLOYS
    • C21C7/00—Treating molten ferrous alloys, e.g. steel, not covered by groups C21C1/00 - C21C5/00
    • C21C7/0006—Adding metallic additives
    • C21C2007/0018—Boron

Definitions

  • the present invention relates to a free-cutting stainless steel material for precision machining that performs forming by cutting at a micrometer level.
  • stainless steel has been used as a material for machining precision parts, taking advantage of its corrosion resistance, but using stainless steel in precision machining is more difficult to cut than using ordinary steel. Therefore, it has been desired to improve the machinability.
  • As a stainless steel with improved machinability sulfur free-cutting stainless steel SUS303 is widely known, but the surface after cutting becomes rough, and it is difficult to use it for micron level precision cutting. It was. That is, conventionally, stainless steel has been considered to be incompatible with machinability and precision workability (surface roughness after cutting). *
  • an object of the present invention is to provide a free-cutting stainless steel material for precision machining that can satisfy both machinability and precision workability, and a method for producing the same.
  • the present invention effectively uses the properties of h-BN (hexagonal boron nitride) particles that are excellent as a solid lubricant and are chemically stable and not affected by acid or alkali.
  • h-BN hexagonal boron nitride
  • Invention 1 is a free-cutting stainless steel material for precision machining that performs molding by cutting at a micrometer level
  • the free-cutting property imparting material is h-BN (hexagonal boron nitride) particles
  • the particle size is A configuration was adopted in which spherical h-BN particles of 200 nm to 5 ⁇ m were dispersed and precipitated in a single state in steel.
  • the single state means a state in which a plurality of h-BN particles or non-metallic inclusion particles other than h-BN and h-BN particles are not aggregated.
  • Invention 2 employs a configuration characterized in that the B content in the free-cutting stainless steel material for precision machining of Invention 1 is 0.003 to 0.1 mass%.
  • Invention 3 employs a configuration characterized in that in the free-cutting stainless steel material for precision machining of Invention 1, the N content is equal to or higher than the B content in a molar ratio.
  • Invention 4 is a free-cutting stainless steel material for precision machining as set forth in any one of Inventions 1 to 3, and has a turning surface characteristic in which the 10-point average roughness (Rz) of the surface roughness of the turning surface is 5 ⁇ m or less. The structure characterized by having was adopted. *
  • Invention 5 employs a configuration characterized in that in the free-cutting stainless steel material for precision machining described in Invention 4, the turning surface characteristics are obtained by turning a round bar having a diameter of 8 mm under the following conditions. .
  • Cutting speed 16 m / min
  • cutting depth 0.2 mm
  • tool feed speed 0.08 mm / rev
  • tool material M30
  • tool shape equilateral triangle
  • cutting fluid not used.
  • Invention 6 is a method for producing a free-cutting stainless steel material for precision machining according to any one of Inventions 1 to 5, wherein B is added with ferroboron or metal boron, and N is dissolved atmosphere (argon + nitrogen) Or the structure characterized by adding to stainless steel molten steel by melt
  • Invention 7 is a method for producing a free-cutting stainless steel material for precision machining according to any one of Inventions 1 to 5, wherein B is added by adding ferroboron or metal boron, and N is added by adding a nitrogen-containing compound.
  • B is added by adding ferroboron or metal boron
  • N is added by adding a nitrogen-containing compound.
  • the structure characterized by adding to molten steel was adopted. *
  • Invention 8 is a method for producing a free-cutting stainless steel material for precision machining according to any one of Inventions 1 to 5, wherein h-BN particles are contained in the structure obtained by the method according to claim 6 or 7.
  • h-BN particles are contained in the structure obtained by the method according to claim 6 or 7.
  • Chemically stable h-BN particles that are not attacked by acid or alkali are dispersed and precipitated in a single state to have excellent machinability as a solid lubricant, excellent cutting accuracy, and deterioration in corrosion resistance.
  • the surface roughness after cutting has a performance similar to or less than that of stainless steel without reworkability, and surface treatment after precision machining is almost unnecessary. .
  • the present invention has the features as described above, and an embodiment thereof will be described below.
  • melting of the free-cutting stainless steel material for precision machining is performed using a melting furnace for melting ordinary stainless steel, in which the melting atmosphere can be adjusted.
  • ferroboron or metal boron is used as a raw material for B (boron), but ferroboron having a low melting point is technically advantageous as a melting raw material, and it is per unit weight of B (boron). Economical due to low market price.
  • the amount of B added is generally 0.003 to 0.1 mass% B, more preferably 0.003 to 0.03 mass% B, as a general guide, the final B content in the free-cutting stainless steel material for precision machining.
  • N nitrogen
  • a nitride of an alloy element that absorbs N in a melting atmosphere or constitutes stainless steel for example, chromium nitride, ferrochromium nitride or the like.
  • N / B should just be 1 or more by molar ratio as a general standard. If the molar ratio of N and B in the free-cutting stainless steel material for precision machining is less than 1, the amount of dissolved B increases and the amount of precipitation of h-BN effective for machinability decreases. Must be 1 or more.
  • the N content depends on the constituent element components in the free-cutting stainless steel material for precision machining, but since B increases the activity of N, the equilibrium N concentration in the steel decreases as B increases.
  • the component composition of SUS304 is 0.25 mass% or less except for dissolution in a pressurized N atmosphere. *
  • the stainless steel molten steel containing B and N produced as described above is cast into a mold to become a free-cutting stainless steel ingot for precision machining.
  • the free-cutting stainless steel ingot for precision machining is formed into a rod, wire, plate, or the like of a free-cutting stainless steel material for precision machining through hot working such as normal forging or rolling.
  • the free-cutting stainless steel material for precision machining after hot working is air-cooled to room temperature.
  • h-BN coarsely grown to about 20-30 ⁇ m is unevenly distributed in a part of the material during the cooling process after hot working. May be generated.
  • H-BN deposited in free-cutting stainless steel for precision machining is dissolved in a relatively short time (for example, 0.5 to 1 hour at 1250 ° C) by maintaining the temperature at 1200 ° C or higher. It can exist in the matrix in a state of being decomposed into B and N. Using this h-BN solid solution phenomenon, heat treatment is performed to re-dissolve h-BN generated in the material in a non-uniform or coarse manner in the material. In addition, since such a process is impossible when the free-cutting stainless steel material for precision processing is melted, it is necessary to perform the process at a temperature lower than the melting temperature. *
  • the quenching operation may be water cooling performed on ordinary stainless steel, but the cooling rate in the temperature range in which h-BN is deposited as described below needs to be a cooling rate that does not cause precipitation.
  • the selection of the tempering temperature is important for precipitating h-BN having a particle size and a distribution state that provides good machinability.
  • the tempering temperature at which a particle size and a distribution state with good machinability are obtained is preferably in the range of 950 to 1100 ° C.
  • the hot working temperature is in a state where h-BN is in solid solution, it is possible to create a state in which B and N are dissolved in supersaturation by quenching after hot working. It is. In such a processing temperature condition, it goes without saying that h-BN solid solution heat treatment at a temperature of 1200 ° C. or higher is unnecessary.
  • the tempering holding time the higher the temperature, the faster the diffusion rate of B and N, so that a shorter time is required, and the range is 0.5 to 3 hours, preferably 1 to 2 hours. Since this tempering heat treatment can also serve as a solution heat treatment performed on general stainless steel, cooling is performed at a cooling rate performed during the solution heat treatment. *
  • the content of B is changed from 0.003 mass% to 0.1 mass%. If the content is 0.003 mass% or less, the effect of cutting is lost, and it exceeds 0.1 mass%. This is because the precipitation of BN increases the tendency of a plurality of h-BN particles to aggregate and the machinability is greatly improved, but adversely affects the surface roughness.
  • N / B is not less than 1 in terms of molar ratio of N is that if it is less than 1, reprecipitation of h-BN during heat treatment of supersaturated B and N cannot be sufficiently achieved. This is because plastic processing becomes difficult because B exists excessively.
  • Example 1 A commercially available austenitic stainless steel (SUS304) round bar (weight 2 kg) was melted as a melting raw material using a cold crucible flotation melting furnace.
  • the component composition (mass%) of the melting raw material was 0.06% C, 0.28% Si, 1.33% Mn, 0.035% P, 0.025% S, 8.05% Ni, 18.39. % Cr.
  • 0.07 MPa of N was sealed in a vacuum induction melting furnace, and the N concentration in the molten steel was adjusted.
  • a predetermined amount of commercially available ferroboron (19.2 mass% B) is added to the molten metal, and the B concentration is adjusted. And ingots were produced.
  • the ingot was forged and rolled at 1200 ° C., processed into a 14 mm square bar, and air-cooled.
  • the rod was held at 1250 ° C. for 0.5 hour, then cooled with water, and further heat treated by holding at 1100 ° C. for 1 hour and then water cooling.
  • Table 1 shows the analytical values of the newly developed steel. Further, as the comparative material 1, the commercially available SUS304 stainless steel used for the melting raw material of Example 1 and the commercially available sulfur free-cutting SUS303 stainless steel as the comparative material 2 were both cut out from a round bar having a diameter of 55 mm and surface roughness was obtained. A test sample was obtained. Table 1 shows analysis values (unit: mass%) of B, N, and S of the melted material. *
  • the surface roughness (10-point average roughness Rz) of a round bar sample cut out from the sample was measured using a scanning laser microscope. Each sample was turned to a diameter of 7.6 mm under the same turning conditions (cutting speed, cutting depth, tool feed speed). The final cutting conditions were cutting speed: 16 m / min, cutting depth: 0.2 mm, tool feed speed: 0.08 mm / rev, tool material: M30, tool shape: equilateral triangle, chip breaker, cutting fluid: non It was use.
  • the measurement results of the surface roughness are shown in Table 2. *
  • the surface roughness of the developed free-cutting stainless steel material for precision machining is improved compared to that of the comparative material 1 (SUS304), and the surface roughness compared to SUS303 of the free-cutting stainless steel of the comparative material 2
  • the roughness has been reduced to about 1/3, which is much improved. This is because, in the developed steel, the fine h-BN particles are dispersed in a single pair state, whereas in the comparative material 2, the MnS particles as the free-cutting imparting substance are coarse and extend like needles. This is due to the formation of a metal structure.
  • FIG. 1 the SEM observation photograph of the broken cross section of the sample cut out from the development steel 2 was shown.
  • FIG. 1 (a) shows a heat treatment in which water is cooled after holding at 1250 ° C. for 0.5 hour, and further, water cooling is carried out after holding at 1100 ° C. for 1 hour, and FIG. 1 (b) is held at 1250 ° C. for 0.5 hour. Then, it is cooled with water, and further subjected to a heat treatment of holding at 850 ° C. for 2 hours and then cooling with water. All the white spherical particles in the figure were found to be h-BN particles by EDS analysis. In the observation surface of FIG.
  • FIG. 2 shows a SEM observation photograph of the cross section of the sample of the comparative material 2 (SUS303). It was confirmed by EDS analysis that the arrows indicate the elongated MnS particles having a diameter of several ⁇ m and a length of several tens of ⁇ m, which are present in the form of fibers in the steel. Table 2 also shows the surface roughness corresponding to the shape of the dropped MnS because the elongated MnS particles appear on the processed surface and fall off during the cutting process. *
  • the present invention makes it possible to easily provide a free-cutting stainless steel material for precision machining that has excellent cutting accuracy and machinability, as well as excellent corrosion resistance and environmental resistance. It was possible to bring excellent usability to the various processing fields used.
PCT/JP2011/053330 2010-04-30 2011-02-17 精密加工用快削ステンレス鋼素材及びその製造方法 WO2011135897A1 (ja)

Priority Applications (2)

Application Number Priority Date Filing Date Title
EP11774682.6A EP2565286A4 (en) 2010-04-30 2011-02-17 STAINLESS STEEL DECOLTAGE MATERIAL FOR PRECISION TREATMENT AND METHOD FOR PRODUCING THE SAME
CN201180021615.7A CN102906290B (zh) 2010-04-30 2011-02-17 精密加工用易切削不锈钢原材料及其制造方法

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JP2010104780A JP6044037B2 (ja) 2010-04-30 2010-04-30 精密加工用快削ステンレス鋼素材及びその製造方法
JP2010-104780 2010-04-30

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EP (1) EP2565286A4 (zh)
JP (1) JP6044037B2 (zh)
CN (1) CN102906290B (zh)
WO (1) WO2011135897A1 (zh)

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* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP2537952B1 (en) * 2010-07-27 2016-12-28 National Institute for Materials Science Free-cutting stainless-steel cast product and process for producing same
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
KR102010052B1 (ko) * 2017-10-19 2019-08-12 주식회사 포스코 열간 압연성이 우수한 중탄소 쾌삭강 및 그 제조방법

Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2001234298A (ja) 2000-02-24 2001-08-28 Sanyo Special Steel Co Ltd オーステナイト系Ｃａ添加快削ステンレス鋼
JP2002038238A (ja) 2000-07-21 2002-02-06 Kiyohito Ishida フェライト系快削ステンレス鋼
JP2004332021A (ja) * 2003-05-01 2004-11-25 Sanyo Special Steel Co Ltd アウトガス特性に優れた非Ｐｂ快削ステンレス鋼
JP2006291296A (ja) * 2005-04-11 2006-10-26 Nisshin Steel Co Ltd 深絞り性に優れたオーステナイト系ステンレス鋼
WO2008016158A1 (fr) 2006-07-31 2008-02-07 National Institute For Materials Science acier inoxydable de découpe libre ET SON PROCÉDÉ DE FABRICATION

Patent Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2001234298A (ja) 2000-02-24 2001-08-28 Sanyo Special Steel Co Ltd オーステナイト系Ｃａ添加快削ステンレス鋼
JP2002038238A (ja) 2000-07-21 2002-02-06 Kiyohito Ishida フェライト系快削ステンレス鋼
JP2004332021A (ja) * 2003-05-01 2004-11-25 Sanyo Special Steel Co Ltd アウトガス特性に優れた非Ｐｂ快削ステンレス鋼
JP2006291296A (ja) * 2005-04-11 2006-10-26 Nisshin Steel Co Ltd 深絞り性に優れたオーステナイト系ステンレス鋼
WO2008016158A1 (fr) 2006-07-31 2008-02-07 National Institute For Materials Science acier inoxydable de découpe libre ET SON PROCÉDÉ DE FABRICATION

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
See also references of EP2565286A4 *

Also Published As

Publication number Publication date
JP2011231387A (ja) 2011-11-17
JP6044037B2 (ja) 2016-12-14
EP2565286A4 (en) 2014-05-07
CN102906290A (zh) 2013-01-30
EP2565286A1 (en) 2013-03-06
CN102906290B (zh) 2015-01-14

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