WO2016104974A1 - Acier inoxydable austénitique présentant une excellente flexibilité - Google Patents

Acier inoxydable austénitique présentant une excellente flexibilité Download PDF

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Publication number
WO2016104974A1
WO2016104974A1 PCT/KR2015/012973 KR2015012973W WO2016104974A1 WO 2016104974 A1 WO2016104974 A1 WO 2016104974A1 KR 2015012973 W KR2015012973 W KR 2015012973W WO 2016104974 A1 WO2016104974 A1 WO 2016104974A1
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WIPO (PCT)
Prior art keywords
stainless steel
austenitic stainless
less
inventive example
excellent flexibility
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PCT/KR2015/012973
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English (en)
Korean (ko)
Inventor
강형구
조규진
채동철
이재화
Original Assignee
주식회사 포스코
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Application filed by 주식회사 포스코 filed Critical 주식회사 포스코
Priority to EP15873501.9A priority Critical patent/EP3239341A4/fr
Priority to CN201580071219.3A priority patent/CN107429367A/zh
Priority to JP2017530337A priority patent/JP2018502991A/ja
Priority to US15/539,874 priority patent/US20170349985A1/en
Publication of WO2016104974A1 publication Critical patent/WO2016104974A1/fr

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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
    • C21D6/004—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
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • 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
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
    • 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
    • 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
    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
    • 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
    • C21D2211/001—Austenite
    • 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
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/10—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of tubular bodies
    • C21D8/105—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of tubular bodies 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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C2202/00—Physical properties

Definitions

  • the present invention relates to an austenitic stainless steel having excellent flexibility.
  • the work hardening is expressed as TS-YS, which is a difference between the yield strength YS indicating the strength at the start of deformation of the material and the tensile strength TS showing the maximum strength by maximizing the work hardening of the material.
  • TS-YS yield strength indicating the strength at the start of deformation of the material
  • TS-YS tensile strength TS showing the maximum strength by maximizing the work hardening of the material.
  • Patent Document 0001 KR 10-2010-0099726 A (2010.09.13)
  • An object of the present invention is to provide an austenitic stainless steel having excellent flexibility by controlling the content of component elements affecting the degree of work hardening and controlling the size of crystal grains in order to solve such a conventional problem.
  • the austenitic stainless steel having excellent flexibility according to the present invention for achieving this object is, in weight%, Si: 0.1 to 0.65%, Mn: 1.0 to 3.0%, Ni: 6.5 to 10.0%, Cr: 16.5 to 18.5%, Cu: 6.0% or less (excluding 0), C + N: 0.13% or less (excluding 0), the rest contains Fe and unavoidable impurities, and the work hardening formula H1 defined by the following formula is 300 or less It is characterized by.
  • the structure size (D) of the austenitic stainless steel excellent in the flexibility of the present invention is characterized by being 20 to 40 ⁇ m.
  • the austenitic stainless steel having excellent flexibility according to the present invention for achieving this object is, in weight%, Si: 0.1 to 0.65%, Mn: 1.0 to 3.0%, Ni: 6.5 to 10.0%, Cr: 16.5 to 18.5%, Cu: 6.0% or less (excluding 0), C + N: 0.13% or less (excluding 0), the rest includes Fe and unavoidable impurities, and the work hardening formula H2 defined by the following formula is 300 or less It is characterized by.
  • the size (D) of the tissue is characterized in that 20 ⁇ 300 ⁇ m.
  • the austenitic stainless steel having excellent flexibility of the present invention has a weight% of Si: 0.1 to 0.65%, Mn: 1.0 to 3.0%, Ni: 6.5 to 10.0%, Cr: 16.5 to 18.5%, and Cu: 6.0%. Or less (excluding 0), C + N: 0.13% or less (excluding 0), the remainder contains Fe and inevitable impurities,
  • M d30 defined by the following formula is characterized in that less than zero.
  • M d30 is -100-0 .
  • TS tensile strength
  • YS yield strength
  • the present invention has the advantage of producing an austenitic stainless steel excellent in flexibility by controlling the content of the element, grain size and the like.
  • 1 is a view showing a correlation between work hardening type H1 and work hardening actual measured value
  • 3 to 5 is a view showing the size distribution of the grains
  • Fig. 6 is a diagram showing a correlation between quartz hardening type H2 and measured hardening degree
  • the austenitic stainless steel excellent in the flexibility of the present invention is, in weight%, Si: 0.1 to 0.65%, Mn: 1.0 to 3.0%, Ni: 6.5 to 10.0%, Cr: 16.5 to 18.5%, Cu: 6.0% And C + N is 0.13% or less and contains the remaining Fe and unavoidable impurities.
  • C and N are not only hardening austenitic stainless steel as an invasive solid solution strengthening element, but if the content is high, hardening strain organic martensite generated during processing increases the work hardening of the material. Therefore, there is a need to limit the content of C and N, the present invention limits the content of C + N to 0.13% or less.
  • Si is added by adjusting in the range of 0.1 to 0.65% by weight.
  • Si is an essential element for deoxidation, 0.1% or more is added.
  • Mn is adjusted and added in the range of 1.0 to 3.0 weight%.
  • Mn is not only essential for deoxidation but also increases stability of the austenite phase, and 1.0% or more is added to maintain austenite balance. However, addition of excessively high content of Mn lowers the corrosion resistance of the material, so the upper limit thereof is limited to 3.0%.
  • Ni is added by adjusting in the range of 6.5 to 10.0% by weight.
  • Ni is not only effective in improving corrosion resistance, such as pitting resistance, by complex addition with Cr, but also softening of austenite steel when its content is increased.
  • Cr is an essential element to improve the corrosion resistance, and more than 16.5% must be added to be used for general purposes. However, addition of excessively high content of Cr causes hardening of the austenite phase and raises the cost, thus limiting the upper limit to 18.5%.
  • Cu is added by adjusting in the range of 6.0 weight% or less.
  • Cu can cause soft nitriding of austenite steel.
  • the addition of excessively high content of Cu lowers the hot workability and rather hardens the austenite phase, so the upper limit thereof is limited to 6.0%.
  • the component control method provided by the present invention is important.
  • the materials described in the following examples were prepared by ingots of 150 mm thickness, hot rolled to 3 mm after heating to 1,250 ° C., and then heat-treated at 1,100 ° C. for 60 seconds.
  • a manufacturing method does not limit the properties of the material provided by the present invention, and is one that employs one of the usual methods for producing austenitic stainless steel, and merely includes an example of manufacturing a material for evaluating the properties.
  • the properties of the material change by the component control method provided in the present invention. Yield strength YS and tensile strength TS are the values obtained by uniaxial stretching of the material.
  • H1 shown in Table 1 is defined by the following equation.
  • the H1 value is defined using the component elements constituting the present invention, and the H1 value and the measured TS-YS value The correlation between them was analyzed.
  • the relationship between the H1 value obtained through component control and the measured TS-YS value is shown, and it can be seen that the above description is implemented.
  • a linearly smooth relationship is established between them, and thus, even if the lower limit of the H1 value is not set in the present invention, austenite having more flexibility through manufacturing a material having a lower H1 value is obtained. It can be seen that the production of the steel can be made.
  • the grain size of the austenitic stainless steel produced by a conventional manufacturing process is generally 30 ⁇ 10 ⁇ m.
  • the grain size (D) of the austenitic stainless steel having excellent flexibility of the present invention is also present in the 30 ⁇ 10 ⁇ m section, as shown in Comparative Example 1 of Table 2 when H1 is 329
  • the actual TS-YS value is obtained as 328, indicating that the flexibility is not good.
  • FIG. 3 to 5 is a view showing the size distribution of the crystal grains
  • Figure 3 is a structure photograph showing the grain size of the austenitic stainless steel according to Inventive Example 6
  • Figure 4 is austenitic stainless steel according to Comparative Example 6 5 is a tissue photograph showing grain size
  • FIG. 5 is a tissue photograph showing grain size of an austenitic stainless steel according to Inventive Example 17.
  • the present invention provides a modified work hardening type H2 to obtain a low work hardening material even when the grain size is larger than usual.
  • Table 3 shows the component contents of Inventive Examples 17 to 21 and Comparative Examples 4 to 6 disclosed in Table 2.
  • the TS-YS value may be limited through the following austenite stability M d30 .
  • the TS-YS value can be maintained at 300 MPa or less, indicating that the flexibility is improved.
  • Austenitic stainless steel having excellent flexibility can be applied to a refrigerant pipe for air conditioners for homes and automobiles.

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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)
  • Heat Treatment Of Sheet Steel (AREA)
  • Materials For Medical Uses (AREA)

Abstract

L'invention concerne un acier inoxydable austénitique présentant une excellente flexibilité. L'acier inoxydable austénitique présentant une excellente flexibilité de la présente invention comprend de 0,1 à 0,65 % en poids de Si, de 1,0 à 3,0 % en poids de Mn, de 6,5 à 10,0 % en poids de Ni, de 16,5 à 18,5 % en poids de Cr, 6,0 % en poids ou moins de Cu (0 exclus), 0,13 % en poids ou moins de C+N (0 exclus), et le reste étant du Fe et des impuretés inévitables, la formule H1 d'écrouissage définie comme une expression mathématique ci-dessous étant de 300 ou moins. H1=-459+79,8 Si-10,2 Mn-8,16 Ni +48,0 Cr -13,2 Cu +623 (C+N)
PCT/KR2015/012973 2014-12-26 2015-12-01 Acier inoxydable austénitique présentant une excellente flexibilité WO2016104974A1 (fr)

Priority Applications (4)

Application Number Priority Date Filing Date Title
EP15873501.9A EP3239341A4 (fr) 2014-12-26 2015-12-01 Acier inoxydable austénitique présentant une excellente flexibilité
CN201580071219.3A CN107429367A (zh) 2014-12-26 2015-12-01 柔韧性优异的奥氏体系不锈钢
JP2017530337A JP2018502991A (ja) 2014-12-26 2015-12-01 可撓性に優れたオーステナイト系ステンレス鋼
US15/539,874 US20170349985A1 (en) 2014-12-26 2015-12-01 Austenitic stainless steels excellent in flexibility

Applications Claiming Priority (2)

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KR1020140191165A KR101659186B1 (ko) 2014-12-26 2014-12-26 가요성이 우수한 오스테나이트계 스테인리스강
KR10-2014-0191165 2014-12-26

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WO2016104974A1 true WO2016104974A1 (fr) 2016-06-30

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US (1) US20170349985A1 (fr)
EP (1) EP3239341A4 (fr)
JP (1) JP2018502991A (fr)
KR (1) KR101659186B1 (fr)
CN (1) CN107429367A (fr)
WO (1) WO2016104974A1 (fr)

Cited By (17)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US20180106557A1 (en) * 2016-03-28 2018-04-19 Lg Electronics Inc. Stainless steel and pipe made thereof
EP3382052A1 (fr) * 2017-03-31 2018-10-03 LG Electronics Inc. Tuyau en acier inoxydable ductile et système de pompe à chaleur le comprenant
EP3598030A4 (fr) * 2017-03-13 2020-12-30 LG Electronics Inc. -1- Climatiseur
EP3598031A4 (fr) * 2017-03-13 2020-12-30 LG Electronics Inc. -1- Climatiseur
EP3598034A4 (fr) * 2017-03-13 2020-12-30 LG Electronics Inc. -1- Climatiseur
EP3598027A4 (fr) * 2017-03-13 2020-12-30 LG Electronics Inc. -1- Climatiseur
EP3598029A4 (fr) * 2017-03-13 2020-12-30 LG Electronics Inc. -1- Appareil de conditionnement d'air
EP3598036A4 (fr) * 2017-03-13 2020-12-30 LG Electronics Inc. -1- Climatiseur
EP3598032A4 (fr) * 2017-03-13 2020-12-30 LG Electronics Inc. -1- Climatiseur
EP3598028A4 (fr) * 2017-03-13 2020-12-30 LG Electronics Inc. -1- Climatiseur
EP3598033A4 (fr) * 2017-03-13 2021-01-13 LG Electronics Inc. Climatiseur
EP3598035A4 (fr) * 2017-03-13 2021-01-13 LG Electronics Inc. Climatiseur
EP3647683A4 (fr) * 2017-06-26 2021-03-24 LG Electronics Inc. Système de pompe à chaleur à gaz
EP3690359A4 (fr) * 2017-09-27 2021-06-23 LG Electronics Inc. Climatiseur
US11457783B2 (en) 2019-06-05 2022-10-04 Lg Electronics Inc. Cleaner
US11519642B2 (en) 2017-06-22 2022-12-06 Lg Electronics Inc. Air conditioner
EP3598025B1 (fr) * 2017-03-13 2024-03-06 LG Electronics Inc. Climatiseur

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EP3239341A1 (fr) 2017-11-01
CN107429367A (zh) 2017-12-01
KR20160079998A (ko) 2016-07-07
US20170349985A1 (en) 2017-12-07

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