EP2060646B1 - Stainless steel sheet for structural members excellent in impact -absorbing characteristics - Google Patents

Stainless steel sheet for structural members excellent in impact -absorbing characteristics Download PDF

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Publication number
EP2060646B1
EP2060646B1 EP07831178.4A EP07831178A EP2060646B1 EP 2060646 B1 EP2060646 B1 EP 2060646B1 EP 07831178 A EP07831178 A EP 07831178A EP 2060646 B1 EP2060646 B1 EP 2060646B1
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EP
European Patent Office
Prior art keywords
impact
strength
deformation
steel sheet
energy absorption
Prior art date
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EP07831178.4A
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German (de)
English (en)
French (fr)
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EP2060646A4 (en
EP2060646A1 (en
Inventor
Junichi Hamada
Haruhiko Kajimura
Fumio Fudanoki
Toshio Tanoue
Ken Kimura
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Nippon Steel Corp
Nippon Steel Stainless Steel Corp
Original Assignee
Nippon Steel and Sumikin Stainless Steel Corp
Nippon Steel and Sumitomo Metal Corp
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Application filed by Nippon Steel and Sumikin Stainless Steel Corp, Nippon Steel and Sumitomo Metal Corp filed Critical Nippon Steel and Sumikin Stainless Steel Corp
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    • 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
    • C22C38/001—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
    • C22C38/06—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
    • 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
    • C22C38/20—Ferrous alloys, e.g. steel alloys containing chromium 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
    • C22C38/34—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/36—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.7% by weight of carbon
    • 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
    • C22C38/42—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

Definitions

  • This invention relates to a stainless steel sheet used chiefly in structural components requiring strength and impact absorption capability, and particularly to a stainless steel sheet for automobile and bus impact absorption components such as front side members, pillars and bumpers, and for structural components such as vehicle suspension members and rims, railcar bodies and the like.
  • Cr-containing stainless steels are far superior to ordinary steels in corrosion resistance and are therefore viewed as having the potential to reduce weight by lowering the corrosion margin (extra thickness to compensate for expected corrosion) and to eliminate the need for painting.
  • austenitic stainless steels are excellent in strength-ductility balance and are considered capable of achieving high strength in combination with high ductility through chemical composition adjustment.
  • collision safety improvement utilizing a steel having high impact absorption capability in the vehicle frame makes it possible, for example, to absorb crash impact by component collapse deformation and thus to lessen the impact on passengers during a collision. In other words, considerable merits can be realized regarding fuel economy improvement through body weight reduction, painting simplification and safety enhancement.
  • Austenitic stainless steels such as SUS301L and SUS304 are used in the structural components of railcars, for instance, because they are excellent in corrosion resistance, ductility and formability.
  • Japanese Patent Publication ( A) No. 2002-20843 teaches an austenitic stainless steel with high strain rate and excellent impact absorption capability that is intended for use mainly in structural components and reinforcing materials for railcars and ordinary vehicles. This is a steel containing 6 to 8% Ni and having an austenite structure that achieves high strength during high-speed deformation owing to the formation of deformation-induced martensite phase.
  • This prior art defines the deformation strengths under dynamic deformation and static deformation, maximum strength, work-hardening index and other properties of the steel.
  • the dynamic/static ratio is defined as the ratio between the maximum dynamic and static strengths. But strength, e.g., yield strength, in the relatively low strain range is strongly affected by the impact absorption property at the time of collision, so the definition based on the maximum strength ratio may become a problem in some cases.
  • martensitic stainless steel sheets imparted with high strength by quenching have very low ductility and are extremely poor in weld toughness. Since automobiles, buses and railcars have many welded structures, their structural reliability is greatly impaired by poor weld toughness.
  • ferritic stainless steel sheets e.g., SUS430
  • SUS430 ferritic stainless steel sheets are low in strength and not suitable for members requiring strength, and they are incapable of improving collision safety performance owing to their low impact energy absorption at the time of high-velocity deformation.
  • the present invention is directed to overcoming the foregoing issues by providing a stainless steel sheet that is both high in strength and excellent in impact absorption property during high-speed deformation.
  • the inventors carried out a study on metal structure in relation to deformation mechanism at the time of sustaining high-speed deformation. As a result, they discovered a technique that enables improvement of impact energy absorption during high-speed deformation of an austenitic stainless steel while simultaneously achieving excellent sheet workability. Specifically, for increasing deformation resistance during ultra-high speed deformation of a strain rate of 10 3 /sec, deformation-induced transformation is positively exploited to increase work hardenability, thereby increasing impact energy absorption through a dramatic improvement in strength and ductility when the component collides. Therefore, a vehicle body fabricated using the steel sheet absorbs the impact at the time of a collision and minimizes body collapse, thereby markedly increasing the safety of passengers.
  • the gist of the present invention is as set out in the following.
  • Total impact energy absorption in dynamic tensile testing is defined as the impact energy absorption up to break when a high-velocity tensile test is conducted at a strain rate of 10 3 /sec corresponding to that at the time of a vehicle collision
  • impact energy absorption to 10% strain is defined as the impact energy absorption up to the 10% strain region in the high-velocity tensile test.
  • the static tensile test is a tensile test conducted at the usual strain rate (strain rate of 10 -3 to -2 /sec).
  • the important point in the present invention is the impact absorption upon incurring a high-speed impact.
  • the impact force at the time of a vehicle collision is applied to structural components of the vehicle.
  • the impact absorption capability of the steel constituting the components is therefore important.
  • Most vehicle structural components have angular cross-sections as typified by hat-shaped formed components.
  • the strain region that absorbs impact differs among different structural components, what is important at locations that collapse during collision is the impact energy absorption up to material destruction.
  • Total impact energy absorption is therefore used as an index.
  • Total impact energy absorption improves as both strength and ductility are higher during high-speed deformation.
  • conventional high-strength steel sheet while high in strength, is low in fracture ductility and is therefore limited in total energy absorption.
  • the inventors carried out a study based on the foregoing indexes, by which they learned that the optimum stainless steel in terms of excellent impact absorption property is an austenitic stainless steel utilizing work hardening by deformation-induced transformation. They further learned that desired impact energy absorption during high-speed deformation can be achieved by adjusting the various constituents to control austenite so that deformation-induced martensite transformation occurs suitably during high-speed deformation.
  • Austenite stability constituting an index of deformation-induced martensite transformation is calculated based on Md 30 value shown below (from the Stainless Steel Handbook compiled by the Japan Stainless Steel Association).
  • the Md 30 value is the temperature at which 50% of martensite is formed at the time of imparting tensile strain to a true strain of 0.3. When impact energy absorption was assessed using this value, it was found that the excellent impact energy absorption prescribed by the present invention could be obtained.
  • Md 30 551 - 462 ⁇ C + N - 9.2 ⁇ Si - 8.1 ⁇ Mn - 13.7 ⁇ Cr - 29 ⁇ Ni + Cu
  • Md 30 551 - 462 ⁇ C + N - 9.2 ⁇ Si - 8.1 ⁇ Mn - 13.7 ⁇ Cr - 29 ⁇ Ni + Cu
  • C must be added to a content of 0.005% or greater to achieve high strength.
  • C content is defined as 0.05% or less, because addition of a large amount degrades formability and weldability. Taking refining cost and grain boundary corrosion property into account, the more preferable content range is 0.01 to 0.02%.
  • N like C
  • N content is defined as 0.30% or less, because excessive addition degrades formability and weldability. Taking refining cost, manufacturability and grain boundary corrosion property into account, the more preferable content range is 0.015 to 0.025%.
  • Si is a deoxidizing element that is also a solution hardening element effective for achieving high strength. For these purposes, it must be added to a content of 0.1% or greater. On the other hand, Si content is defined as 2% or less, because addition of a large amount degrades formability and markedly lowers the dynamic/static ratio. Taking manufacturability into account, the more preferable content range is 0.2 to 1%.
  • Mn is a deoxidizing element and a solution hardening element effective for achieving high strength. Mn also promotes work hardening of austenite phase during high-speed deformation. For these purposes, it must be added to a content of 0.1% or greater. On the other hand, Mn content is defined as 15% or less, because when added in a large amount, deformation-induced martensite is not formed and formation of MnS, which is a water-soluble inclusion, degrades corrosion resistance. Taking descaling property in the manufacturing process into account, the more preferable content range is 1 to 10%.
  • Ni is an element that improves corrosion resistance. For this, and for austenite phase formation, Ni must be present at a content of 0.5% or greater. On the other hand, Ni content is defined as 8% or less, because when added in a large amount, raw material cost is markedly higher and deformation-induced martensite is not formed. Taking manufacturability, stress corrosion cracking and the like into account, the more preferable content range is 1.5 to 7.5%.
  • Cu improves formability and contributes to dynamic/static ratio improvement. It is added to a content of 0.1% or greater. Cu also produces its effects when included from scrap or the like in the composition adjustment process. When added in excess of 5%, however, deformation-induced martensite formation no long occurs, so the content is defined as 5% or less. The more preferable range is 0.1 to 4%.
  • Cr is an important element that must be added to a content of 11% or greater from the viewpoint corrosion resistance.
  • the upper limit of Cr addition is defined as 20%, because excessive addition necessitates addition of large amounts of other elements for structure regulation.
  • the content range is preferably 14 to 18%.
  • Al is added as a deoxidizing element and also because it renders sulfides harmless and contributes to improvement of workability aspects such as hole expandability during component processing. These effects appear at an Al content of 0.01% or greater, so the lower limit of content is defined as 0.01%.
  • the upper content limit is defined as 0.5%, because addition in excess of this level leads to surface flaw occurrence and manufacturability degradation. Taking cost and the like into account, the more preferable content range is 0.1 to 0.5%.
  • the present invention provides a steel having much higher impact absorption property than the conventional high-strength steel, wherein the total impact energy absorption is defined as 500 MJ/m 3 or greater and, from FIG.s. 1 and 2 , the range of Md 30 value is defined as 0 to 100 °C.
  • the impact energy absorption to 10% strain obtained is 50 MJ/m 3 or greater.
  • Studies conducted by the inventors showed that if impact energy absorption of 50 MJ/m 3 can be obtained, that is adequate as the impact absorption property in the relatively low strain region. So the impact energy absorption to 10% strain is defined as 50 MJ/m 3 or greater. No upper limit value is defined for the impact energy absorption because the effect of the present invention can be realized without defining one.
  • the stainless steel of the present invention is intended for fabrication into structural components. It is therefore important for it to have good formability. As pointed out earlier, most vehicle structural components have angular cross-sections as typified by hat-shaped formed components. As the fabrication involves bending and drawing, the steel requires ductility. A study was carried out regarding methods of fabricating impact absorption components. It was found with regard to steel for which tensile strength was 600 MPa or greater in static tensile testing, adequate forming was possible if elongation at break was 40% or greater. Elongation at break in static tensile testing was therefore defined as 40% or greater.
  • Some components require high strength of 700 MPa or greater.
  • Such high-strength steels are adjusted in strength by cold rolling and annealing followed by temper rolling. Although no upper limit of strength is necessary from the material aspect, the upper limit is defined as 1600 MPa in view of manufacturing and practical concerns.
  • temper rolling is conducted, the reduction can be set in accordance with the required strength level. However, taking manufacturability into consideration, it is preferably around 1 to 70%.
  • the steel sheet manufactured in this manner is reduced in elongation at break in static tensile testing.
  • the elongation at break in static tensile testing of a steel sheet of the foregoing tensile strength level is required to be 5% or greater. It is therefore defined as 5% or greater and is preferably 10% or greater.
  • the method of manufacturing the steel sheet of the present invention is not particularly defined and the product thickness can be decided based on requirements.
  • the hot rolling conditions, hot rolled sheet thickness, hot rolled sheet and cold rolled sheet annealing temperature and atmosphere, and other matters can be suitably selected. No special equipment is required in connection with the pass schedule, cold rolling reduction and roll diameter in cold rolling, and efficient use of existing equipment suffices. Use/non-use of lubricant during temper rolling, the number of temper rolling passes and the like are also not particularly specified. If desired, shape correction utilizing a tension leveler can be applied after cold rolling and annealing or after temper rolling.
  • the product structure is fundamentally austenite, formation of a second phase, such as of ferrite or martensite, is also acceptable.
  • Table 1 includes examples corresponding to claims 1 to 6.
  • the steels having chemical compositions prescribed by the present invention were superior to the comparison steels in both total impact energy absorption to destruction and impact energy absorption in the low strain region to 10% strain, so that that they were excellent in impact absorption property.
  • Such steels are suitable for use in impact absorption components at risk of experiencing relatively large deformation
  • the steels were also suitable for formation into complex structural members, as evidenced by their high elongation at break and excellent ductility in static tensile testing.
  • Table 2 includes examples corresponding to claim 7.
  • the invention examples whose temper rolling reduction was adjusted to achieve tensile strength of 700 MPa or greater and elongation at break is 5% or greater, exhibited high impact energy absorption to 10% strain of 50 MJ/m 3 or greater in dynamic tensile testing, as well as a dynamic/static ratio of 1.4 or greater, making them suitable for use in high-strength members required to absorb impact in the low strain region.
  • the present invention enables provision of a high-strength stainless steel sheet excellent in impact absorption capability even without addition of large amounts of alloying elements.
  • the stainless steel sheet manifests outstanding industrial usefulness, including environmental protection through weight reduction and improved collision safety, especially when utilized in the structural components of transport means such as automobiles, buses and railcars.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
EP07831178.4A 2006-12-27 2007-10-30 Stainless steel sheet for structural members excellent in impact -absorbing characteristics Active EP2060646B1 (en)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
JP2006350722A JP5165236B2 (ja) 2006-12-27 2006-12-27 衝撃吸収特性に優れた構造部材用ステンレス鋼板
PCT/JP2007/071445 WO2008078457A1 (ja) 2006-12-27 2007-10-30 衝撃吸収特性に優れた構造部材用ステンレス鋼板

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EP2060646A1 EP2060646A1 (en) 2009-05-20
EP2060646A4 EP2060646A4 (en) 2014-01-01
EP2060646B1 true EP2060646B1 (en) 2015-06-17

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US (1) US20100233015A1 (zh)
EP (1) EP2060646B1 (zh)
JP (1) JP5165236B2 (zh)
KR (1) KR20080106200A (zh)
CN (1) CN101410543B (zh)
WO (1) WO2008078457A1 (zh)

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JP5056985B2 (ja) * 2009-11-18 2012-10-24 住友金属工業株式会社 オーステナイト系ステンレス鋼板およびその製造方法
KR20120132691A (ko) * 2010-04-29 2012-12-07 오또꿈뿌 오와이제이 높은 성형성을 구비하는 페라이트-오스테나이트계 스테인리스 강의 제조 및 사용 방법
FI125442B (fi) * 2010-05-06 2015-10-15 Outokumpu Oy Matalanikkelinen austeniittinen ruostumaton teräs ja teräksen käyttö
WO2013154071A1 (ja) * 2012-04-10 2013-10-17 新日鐵住金株式会社 衝撃吸収部材に適した鋼板とその製造方法
ITRM20120647A1 (it) * 2012-12-19 2014-06-20 Ct Sviluppo Materiali Spa ACCIAIO INOSSIDABILE AUSTENITICO AD ELEVATA PLASTICITÀ INDOTTA DA GEMINAZIONE, PROCEDIMENTO PER LA SUA PRODUZIONE, E SUO USO NELLÂeuro¿INDUSTRIA MECCANICA.
WO2015087376A1 (ja) * 2013-12-09 2015-06-18 新日鐵住金株式会社 オーステナイト系ステンレス鋼板およびその製造方法
KR101659186B1 (ko) * 2014-12-26 2016-09-23 주식회사 포스코 가요성이 우수한 오스테나이트계 스테인리스강
JP6477181B2 (ja) * 2015-04-07 2019-03-06 新日鐵住金株式会社 オーステナイト系ステンレス鋼
KR101952818B1 (ko) * 2017-09-25 2019-02-28 주식회사포스코 강도 및 연성이 우수한 저합금 강판 및 이의 제조방법
CN107747025B (zh) * 2017-11-02 2019-08-16 浙江双森金属科技股份有限公司 一种不锈钢管及其加工工艺
KR102326262B1 (ko) * 2019-12-18 2021-11-15 주식회사 포스코 고항복비 고강도 오스테나이트계 스테인리스강
KR102385472B1 (ko) * 2020-04-22 2022-04-13 주식회사 포스코 고강도, 고성형의 저원가 오스테나이트계 스테인리스강 및 그 제조방법
KR102403849B1 (ko) * 2020-06-23 2022-05-30 주식회사 포스코 생산성 및 원가 절감 효과가 우수한 고강도 오스테나이트계 스테인리스강 및 이의 제조방법

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JP5165236B2 (ja) 2013-03-21
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JP2008163358A (ja) 2008-07-17
CN101410543A (zh) 2009-04-15
US20100233015A1 (en) 2010-09-16
CN101410543B (zh) 2011-04-06
EP2060646A4 (en) 2014-01-01
EP2060646A1 (en) 2009-05-20

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