WO2011161927A1 - Procédé de fabrication d'un tuyau en acier - Google Patents

Procédé de fabrication d'un tuyau en acier Download PDF

Info

Publication number
WO2011161927A1
WO2011161927A1 PCT/JP2011/003495 JP2011003495W WO2011161927A1 WO 2011161927 A1 WO2011161927 A1 WO 2011161927A1 JP 2011003495 W JP2011003495 W JP 2011003495W WO 2011161927 A1 WO2011161927 A1 WO 2011161927A1
Authority
WO
WIPO (PCT)
Prior art keywords
steel pipe
temperature
quenching
less
manufacturing
Prior art date
Application number
PCT/JP2011/003495
Other languages
English (en)
Japanese (ja)
Inventor
内田　和宏
Original Assignee
住友金属工業株式会社
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by 住友金属工業株式会社 filed Critical 住友金属工業株式会社
Priority to JP2011526332A priority Critical patent/JPWO2011161927A1/ja
Publication of WO2011161927A1 publication Critical patent/WO2011161927A1/fr

Links

Images

Classifications

    • 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
    • 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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/08—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for tubular bodies or pipes
    • 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
    • C21D9/08—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for tubular bodies or pipes
    • C21D9/085—Cooling or quenching
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • C—CHEMISTRY; METALLURGY
    • 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
    • C21D1/06—Surface hardening
    • C21D1/09—Surface hardening by direct application of electrical or wave energy; by particle radiation
    • C21D1/10—Surface hardening by direct application of electrical or wave energy; by particle radiation by electric induction
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/008—Martensite
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
    • Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
    • Y02P10/00—Technologies related to metal processing
    • Y02P10/25—Process efficiency

Definitions

  • the present invention relates to a method of manufacturing a steel pipe by quenching by high-frequency induction heating, and more particularly to a method of manufacturing a steel pipe capable of obtaining a high-strength and high-toughness steel pipe.
  • accumulators made using steel pipes are often used.
  • the accumulator using the steel pipe is filled with high-pressure gas, and the high-pressure gas sealed in the accumulator is ejected into the airbag at a time when the airbag is activated. Therefore, steel pipes used in accumulators are subjected to stress at a large strain rate in a very short time, so high strength, high toughness and excellent burst resistance are required in addition to high dimensional accuracy, workability and weldability. Is done.
  • the steel pipe used for such an air bag is a steel pipe made of steel by hot pipe making, quenched and tempered after being heated and then tempered on the steel pipe, and then cold worked to finish the steel pipe to a predetermined dimension, It may be manufactured by removing the residual stress by annealing.
  • Quenching and tempering are applied to the steel pipe to ensure the strength and toughness required for the steel pipe for airbags.
  • the toughness of the steel pipe which is reduced by cold working, should be adjusted by adding alloy components to the steel material. Need to compensate.
  • alloy components are added to steel, it is difficult to thin the steel pipe by hot pipe making, and high-strength steel pipes that have been quenched and tempered are cold-worked. It becomes difficult to reduce the thickness.
  • an increase in raw material cost due to the addition of alloy components is also a problem.
  • the steel is made into steel pipe by hot pipe making and steel pipe by cold working.
  • a method of manufacturing a steel pipe for an air bag is studied in which the steel pipe is quenched by induction induction heating and then tempered.
  • the toughness of the steel pipe can be ensured by quenching and tempering performed after the cold working, and it is not necessary to add an alloy component to the steel material. For this reason, while thinning by hot pipe making and cold work becomes easy, the raise of the raw material cost by addition of an alloy component can be suppressed.
  • Patent Document 1 is available.
  • a steel material having a predetermined steel composition is made into a steel pipe by hot pipe making, quenching after heating to the steel pipe and quenching, and tempering at a temperature below the Ac 1 transformation point.
  • the steel pipe is finished to a predetermined dimension by cold working.
  • the workability area reduction rate
  • the X-ray integrated intensity ratio of the ⁇ 110 ⁇ plane measured in a cross section perpendicular to the axial direction L of the steel pipe is perpendicular to the circumferential direction T of the steel pipe.
  • the ratio of the ⁇ 110 ⁇ plane to the X-ray integral intensity ratio measured with a simple cross section is set to 50 or less, and excellent burst resistance can be ensured.
  • quenching performed on a steel pipe is rapidly heated to a quenching temperature and then held for a short time and rapidly cooled.
  • the quenching temperature is 900 to 1000 ° C.
  • the heating means is preferably high frequency induction heating.
  • a steel material having a predetermined steel composition is made into a steel pipe by hot pipe making, and the steel pipe is finished to a predetermined size by cold working, and then 900 to 960 ° C.
  • the steel pipe is subjected to quenching and tempering to make the austenite grain size 11.0 or more.
  • it is supposed that the strength and toughness required for a steel pipe for an airbag can be secured by setting the austenite grain size to 11.0 or more.
  • a steel material having a predetermined steel composition is made into a steel pipe by hot pipe making, and after finishing the steel pipe to a predetermined dimension by cold working, the temperature of the Ac 3 transformation point
  • the steel pipe is subjected to quenching as described above and tempering at a temperature equal to or lower than the Ac 1 transformation point.
  • the quenching applied to the steel pipe is preferably rapidly heated to the quenching temperature, then held for a short time and rapidly cooled.
  • the quenching temperature is 900 to 1000 ° C., and the heating means is preferably high frequency induction heating.
  • the steel pipe for an air bag can be used even if the steel pipe is quenched and tempered while satisfying the conditions described therein. In some cases, the strength and toughness required by the method cannot be secured.
  • the present invention has been made in view of such a situation, and the steel pipe having high strength and high toughness is obtained by completely martensifying the structure of the steel pipe by quenching and tempering and by refining the crystal grains. It aims at providing the manufacturing method of the steel pipe which can obtain.
  • the present inventor has found that the time required for rapid cooling to start after the temperature of the high-frequency induction heated steel pipe reaches the temperature of the Ac 3 transformation point. And the temperature at which induction heating is performed during quenching. As a result, it has been found that a steel pipe having high strength and high toughness can be obtained by making the structure of the steel pipe subjected to quenching and tempering completely martensite and making the crystal grains finer.
  • the steel pipe is heated to a quenching temperature defined by the following formula (1) by high-frequency induction heating, and the temperature of the high-frequency induction heated steel pipe reaches the temperature of the Ac 3 transformation point.
  • a quenching temperature 975 ° C. or higher
  • the time required to start the rapid cooling after reaching is 6 seconds or less
  • the quenching temperature is lower than 975 ° C. and 950 ° C. or higher
  • the quenching temperature is 8 seconds or less.
  • the manufacturing method of the steel pipe is characterized in that it is 9 seconds or less.
  • T1 is the quenching temperature (° C.)
  • TAc3 is the temperature of the Ac 3 transformation point (° C.).
  • temperature of the steel pipe means a temperature determined based on an outer surface temperature measured by a radiation thermometer on the outlet side (downstream side) of the high-frequency induction heating device (heating coil).
  • the quenching temperature T1 is a temperature measured by a radiation thermometer on the exit side of the high-frequency induction heating device, and the temperature of the steel pipe in the process of high-frequency induction heating is the quenching temperature T1 (that is, the radiation thermometer on the exit side). ) And the heating rate.
  • the steel pipe manufacturing method of the present invention has the following remarkable effects. (1) By defining the time required for the quenching to start after the temperature of the steel pipe reaches the temperature of the Ac 3 transformation point and the quenching temperature, the structure of the obtained steel pipe is completely martensitic and crystallized. By refining the grains, a steel pipe with high strength and high toughness can be obtained. (2) By performing quenching and tempering after cold working, it is easy to reduce the thickness in hot pipe making and cold working, and it is possible to suppress an increase in raw material cost due to the addition of alloy components.
  • FIG. 1 is a diagram for explaining the time required from the time when the temperature of a steel pipe specified in the present invention reaches the temperature of the Ac 3 transformation point until the rapid cooling starts, and the steel pipe is quenched by the method of manufacturing a steel pipe according to the present invention. It is a figure which shows the relationship between the time at the time of giving, and the temperature of a steel pipe.
  • FIG. 2 shows that the time required for quenching to start after the temperature of the steel pipe at the time of quenching reaches the temperature of the Ac 3 transformation point and the quenching temperature depend on the hardness and austenite grain size of the heat-treated specimen. It is a figure which shows the influence which acts.
  • the steel pipe when the steel pipe is quenched after being heated, the steel pipe is heated to a quenching temperature defined by the following formula (1) by high-frequency induction heating, and the temperature of the steel pipe heated by high-frequency induction is Ac.
  • the time required to start rapid cooling after reaching the temperature of the third transformation point is 6 seconds or less when the quenching temperature is 975 ° C. or more, and 8 seconds or less when the quenching temperature is less than 975 ° C. and 950 ° C. or more.
  • the quenching temperature is less than 950 ° C., it is set to 9 seconds or less.
  • T1 is the quenching temperature (° C.)
  • TAc3 is the temperature of the Ac 3 transformation point (° C.).
  • FIG. 1 is a diagram for explaining the time required from the time when the temperature of the steel pipe specified in the present invention reaches the temperature of the Ac 3 transformation point until the rapid cooling starts, and the steel pipe is quenched by the method of manufacturing the steel pipe of the present invention. It is a figure which shows the relationship between the time at the time of giving, and the temperature of a steel pipe. As shown in the figure, in the method for manufacturing a steel pipe according to the present invention, the time required from when the temperature of the high-frequency induction heated steel pipe reaches the temperature of the Ac 3 transformation point to start quenching is managed.
  • the temperature of the high-frequency induction-heated steel pipe decreases between the time of heating to the quenching temperature and the time of rapid cooling.
  • the time required from when the structure of the heated steel pipe reaches the temperature of the Ac 3 transformation point at which austenitization starts to start quenching is managed.
  • the quenching temperature is outside the range defined by the above formula (1) and becomes less than the temperature obtained by adding 40 ° C. to the temperature of the Ac 3 transformation point, as shown in FIG. May not be fully martensitic and may lack strength and toughness.
  • the quenching temperature exceeds 1000 ° C. outside the range defined by the above formula (1), the crystal grain size of the steel pipe is coarsened by heating, the austenite crystal grain size of the resulting steel pipe is lowered, and the toughness is insufficient.
  • the time required from when the temperature of the steel pipe reaches the temperature of the Ac 3 transformation point to start quenching is 6 seconds or less when the quenching temperature is 975 ° C. or more, and the quenching temperature is less than 975 ° C. and 950 ° C. or more. If the quenching temperature is less than 950 ° C., it is 9 seconds or less. This is to prevent the austenite crystal grain size of the obtained steel pipe from being lowered and the toughness being insufficient as shown in FIG.
  • Quenching using high-frequency induction heating is generally performed by sequentially arranging a coil for high-frequency induction heating of a steel pipe and a cooling zone for cooling the heated steel pipe, and feeding the steel pipe by a conveying device such as a roller.
  • the steel pipe is subjected to high-frequency induction heating to the quenching temperature by passing through the water, and when passing through the cooling zone, cooling water or the like is injected to quench the steel pipe.
  • the temperature of a steel pipe is measured using the radiation thermometer arrange
  • the temperature measured by this radiation thermometer is the temperature of the steel pipe immediately after coming out of the high frequency induction heating device, and is the highest temperature in quenching, and corresponds to the quenching temperature T1.
  • the steel pipe is passed through the heating device and induction-heated at high frequency, the steel pipe reaches the temperature of the Ac 3 transformation point in the heating device, but it is difficult to measure the temperature of the steel pipe in the heating device.
  • the heating rate is the same pattern.
  • the temperature of the steel pipe in the process of induction heating can be estimated from the quenching temperature T1 (that is, the temperature measured by the radiation thermometer on the exit side) and the heating rate. The time when the temperature of the steel pipe reaches the temperature of the Ac 3 transformation point can be grasped.
  • the heating rate (° C./s) is difficult to confirm directly, for example, assuming that the heating rate during high-frequency induction heating is constant, the temperature (° C.) of the steel pipe measured by the radiation thermometer on the outlet side ) And the temperature (° C.) of the steel pipe before heating (incoming side) can be derived by dividing by the heating time (s). Further, the heating time can be calculated from the conveying speed of the steel pipe and the length of the heating device.
  • the time required for the quenching to start after the temperature of the steel pipe reaches the temperature of the Ac 3 transformation point includes the heating device and the cooling zone. It can be adjusted by changing the interval at the time of placement or the feed speed of the transport device.
  • the raw pipe obtained by hot pipe making is finished to a predetermined dimension by cold working to form a steel pipe, and the steel pipe is subjected to the above-mentioned quenching, and then the temperature of the Ac 1 transformation point or lower. It is preferable to temper the steel pipe.
  • the required toughness can be ensured by quenching and tempering after cold working, so there is no need to add alloy components to the steel material, and thinning by hot pipe making and cold working is eliminated. This is because it becomes easy and an increase in raw material cost due to the addition of alloy components can be suppressed.
  • the method of manufacturing a steel pipe according to the present invention when quenching is performed on the steel pipe using high-frequency induction heating, it is necessary to start quenching after the quenching temperature and the temperature of the steel pipe reach the temperature of the Ac 3 transformation point. Specify time. Thereby, the structure of the obtained steel pipe is completely martensitic and crystal grains are refined. For this reason, since the obtained steel pipe is high strength and toughness, it is suitable for the steel pipe for airbags used for an accumulator by the airbag system of a motor vehicle.
  • Test method The test was performed by subjecting the solid round bar test piece to heat treatment by high-frequency induction heating to the quenching temperature, followed by quenching and quenching, and then tempering at a temperature below the Ac 1 transformation point.
  • the time required for rapid cooling to start after the temperature of the high-frequency induction heated steel pipe reaches the temperature of the Ac 3 transformation point during heat treatment varies in the range of 0.2 to 9 seconds in each test. I let you.
  • the quenching temperature was varied in the range of 830 to 1050 ° C. in each test.
  • Test pieces Outer diameter 3mm, length 6mm Material C: 0.16% by mass, Mo: 0.01% by mass, Cr: 0.30% by mass, Ni: 0.26% by mass and Cu: 0.25% by mass of carbon steel Ac 3 transformation point Temperature 832 ° C
  • evaluation indexes the hardness and austenite grain size of the heat-treated specimen were measured. Hardness measured the value of HV10 by the test force 98.07N according to the method prescribed
  • pass / fail was judged based on a hardness of 380 HV or more and an austenite grain size of 11 or more.
  • the criterion for the hardness was 380 HV, which is the hardness when the structure of a steel material containing 0.16% by mass of C is 95% by mass or more. That is, when the hardness is equal to or higher than the criterion, it is considered that the structure of the test piece is completely martensitic.
  • FIG. 2 shows that the time required for quenching to start after the temperature of the steel pipe at the time of quenching reaches the temperature of the Ac 3 transformation point and the quenching temperature depend on the hardness and austenite grain size of the heat-treated specimen. It is a figure which shows the influence which acts. In this figure, the time (seconds) required to start quenching after the temperature of the steel pipe at the time of quenching reaches the temperature of the Ac 3 transformation point is plotted on the horizontal axis using a logarithmic scale, and the quenching temperature (° C) is plotted on the vertical axis. Show.
  • heat-treated specimens with hardness and austenite crystal grain size that are both above the standard value are black circles, and those with hardness above the standard value and austenite crystal grain size below the standard value are outlined. In the triangle marks, those whose hardness and austenite grain size are both less than the standard value are indicated by x marks.
  • the Ac 3 transformation point of the test piece is 832 ° C.
  • the quenching temperature is less than 872 ° C. and falls outside the range defined by the above equation (1), as shown in FIG. Both austenite grain sizes were below the standard value.
  • the quenching temperature exceeded 1000 ° C. and was outside the range defined by the above formula (1), in all cases, the austenite grain size was less than the standard value, and in part, the hardness was also less than the standard value.
  • the quenching temperature is 1000 ° C. or less and 975 ° C. or more
  • the time required for the quenching to start after the steel pipe temperature reaches the Ac 3 transformation point exceeds 6 seconds, and the quenching temperature is less than 975 ° C.
  • the austenite grain size was less than the reference value in all cases where the temperature required was 8 ° C or more after the temperature of the steel pipe reached the temperature of the Ac 3 transformation point and the rapid cooling started.
  • the quenching temperature is within the range defined by the above formula (1), and the time required for the quenching to start after the temperature of the steel pipe reaches the temperature of the Ac 3 transformation point is 975 ° C. or higher. 6 seconds or less, 8 seconds or less when the quenching temperature is less than 975 ° C. and 950 ° C. or more, 9 seconds or less when the quenching temperature is less than 950 ° C., and heat treatment was performed according to the conditions specified in the present invention. All of the test pieces had hardness and austenite grain size equal to or larger than the standard values.
  • the time required for the steel pipe to be heated to the quenching temperature defined by the above formula (1) and the steel pipe temperature to reach the temperature of the Ac 3 transformation point to start quenching is defined by the present invention. It was confirmed that by performing quenching in the range, the heat-treated test piece had a hardness and austenite grain size equal to or higher than the reference value. Therefore, it has been clarified that the structure of the obtained steel pipe can be completely martensite and the crystal grains can be refined by the steel pipe manufacturing method of the present invention.
  • the steel pipe manufacturing method of the present invention has the following remarkable effects. (1) By defining the time required for the quenching to start after the temperature of the steel pipe reaches the temperature of the Ac 3 transformation point and the quenching temperature, the structure of the obtained steel pipe is completely martensitic and crystallized. By refining the grains, a steel pipe with high strength and high toughness can be obtained. (2) By performing quenching and tempering after cold working, it is easy to reduce the thickness in hot pipe making and cold working, and it is possible to suppress an increase in raw material cost due to the addition of alloy components.
  • the steel pipe manufacturing method of the present invention can provide a steel pipe with high strength and high toughness, it is useful for manufacturing a steel pipe for an airbag used for an accumulator in an automobile airbag system.

Landscapes

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

Abstract

Dans le procédé de fabrication d'un tuyau en acier ci-décrit, quand une trempe est appliquée à un tuyau en acier préalablement chauffé, le tuyau est chauffé à une température de trempe définie par la formule (1) par induction haute fréquence, et le temps nécessaire entre le moment où la température du tuyau chauffé par induction haute fréquence atteint la température correspondant au point de transformation Ac3 et le moment où un refroidissement rapide est initié ne dépasse pas 6 secondes si la température de trempe est supérieure ou égale à 975 °C, 8 secondes si la température de trempe est supérieure ou égale à 950 °C, mais inférieure à 975 °C, et 9 secondes si la température de trempe est inférieure à 950 °C. Ainsi, la structure du tuyau en acier subit une transformation martensitique complète, et un tuyau en acier résistant et tenace peut être obtenu car les grains cristallins sont miniaturisés. Dans la formule (1), T1 est la température de trempe (°C), et TAc3 et la température du point de transformation Ac3 (°C). (1) TAc3 + 40 °C ≤ T1 ≤ 1000 °C.
PCT/JP2011/003495 2010-06-21 2011-06-20 Procédé de fabrication d'un tuyau en acier WO2011161927A1 (fr)

Priority Applications (1)

Application Number Priority Date Filing Date Title
JP2011526332A JPWO2011161927A1 (ja) 2010-06-21 2011-06-20 鋼管の製造方法

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
JP2010-140045 2010-06-21
JP2010140045 2010-06-21

Publications (1)

Publication Number Publication Date
WO2011161927A1 true WO2011161927A1 (fr) 2011-12-29

Family

ID=45371134

Family Applications (1)

Application Number Title Priority Date Filing Date
PCT/JP2011/003495 WO2011161927A1 (fr) 2010-06-21 2011-06-20 Procédé de fabrication d'un tuyau en acier

Country Status (2)

Country Link
JP (1) JPWO2011161927A1 (fr)
WO (1) WO2011161927A1 (fr)

Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2013094116A1 (fr) * 2011-12-21 2013-06-27 新日鐵住金株式会社 Procédé de fabrication d'un tube en acier pour un coussin de sécurité gonflable
CN106498130A (zh) * 2016-10-27 2017-03-15 贵州大学 在含硅合金钢中形成微纳尺度孪晶马氏体的工艺方法

Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS5819438A (ja) * 1981-07-28 1983-02-04 Sumitomo Metal Ind Ltd 高強度・高靭性を有する鋼管の製造方法
JP2002194501A (ja) * 2000-12-27 2002-07-10 Sumitomo Metal Ind Ltd 高強度高靱性エアバッグ用鋼管とその製造方法
JP2002294339A (ja) * 2001-03-29 2002-10-09 Sumitomo Metal Ind Ltd 高強度エアバッグ用鋼管の製造方法
JP2007262469A (ja) * 2006-03-28 2007-10-11 Jfe Steel Kk 鋼管およびその製造方法
JP2010132999A (ja) * 2008-12-08 2010-06-17 Sumitomo Metal Ind Ltd エアバッグ用鋼管とその製造方法

Patent Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS5819438A (ja) * 1981-07-28 1983-02-04 Sumitomo Metal Ind Ltd 高強度・高靭性を有する鋼管の製造方法
JP2002194501A (ja) * 2000-12-27 2002-07-10 Sumitomo Metal Ind Ltd 高強度高靱性エアバッグ用鋼管とその製造方法
JP2002294339A (ja) * 2001-03-29 2002-10-09 Sumitomo Metal Ind Ltd 高強度エアバッグ用鋼管の製造方法
JP2007262469A (ja) * 2006-03-28 2007-10-11 Jfe Steel Kk 鋼管およびその製造方法
JP2010132999A (ja) * 2008-12-08 2010-06-17 Sumitomo Metal Ind Ltd エアバッグ用鋼管とその製造方法

Cited By (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2013094116A1 (fr) * 2011-12-21 2013-06-27 新日鐵住金株式会社 Procédé de fabrication d'un tube en acier pour un coussin de sécurité gonflable
JP2013129875A (ja) * 2011-12-21 2013-07-04 Nippon Steel & Sumitomo Metal Corp エアバック用鋼管の製造方法
CN104011233A (zh) * 2011-12-21 2014-08-27 新日铁住金株式会社 安全气囊用钢管的制造方法
EP2796572A4 (fr) * 2011-12-21 2015-08-05 Nippon Steel & Sumitomo Metal Corp Procédé de fabrication d'un tube en acier pour un coussin de sécurité gonflable
CN106498130A (zh) * 2016-10-27 2017-03-15 贵州大学 在含硅合金钢中形成微纳尺度孪晶马氏体的工艺方法

Also Published As

Publication number Publication date
JPWO2011161927A1 (ja) 2013-08-19

Similar Documents

Publication Publication Date Title
TWI679285B (zh) 熱軋鋼板及其製造方法
EP3239339B1 (fr) Produit moulé à base d'un acier apte au traitement thermique, avec résistance à la traction ultra-elevée ayant une excellente durabilité et procédé de fabrication correspondant
JP6341214B2 (ja) 熱間成形鋼板部材およびその製造方法ならびに熱間成形用鋼板
RU2680042C2 (ru) Способ производства высокопрочного стального листа, обладающего улучшенной прочностью, пластичностью и формуемостью
US8518195B2 (en) Heat treatment for producing steel sheet with high strength and ductility
JP5668337B2 (ja) 延性及び耐遅れ破壊特性に優れる超高強度冷延鋼板およびその製造方法
EP2562272B1 (fr) Méthode pour la production d'un produit d'acier avec des propriétés mécaniques excellentes, le produit fabriqué par ladite méthode et l'utilisation des produits
CA2585629A1 (fr) Tuyau en acier pour dispositif de gonflage d'un air bag et procede de production de celui-ci
EP3222742A1 (fr) Barre en acier laminé ou matériau de fil laminé destiné à un composant forgé à froid
US11401569B2 (en) High-strength cold-rolled steel sheet and method for manufacturing same
EP3222743A1 (fr) Barre d'acier laminé ou matériau laminé filaire pour élément forgé à froid
CN104781438A (zh) 汽车用碰撞能量吸收构件及其制造方法
KR101986876B1 (ko) 고연신율을 갖는 초고강도 재료의 생산 방법
WO2015151448A1 (fr) Tuyau en acier sans soudure pour un tuyau d'injection de carburant
JP4983082B2 (ja) 高強度鋼材及びその製造方法
JP5234226B2 (ja) エアバッグ用鋼管の製造方法
JP6816355B2 (ja) 熱延鋼板およびその製造方法
CN109477181B (zh) 高强度钢板及其制造方法
WO2011161927A1 (fr) Procédé de fabrication d'un tuyau en acier
JP2009203492A (ja) 自動車構造部材用高張力溶接鋼管およびその製造方法
CA3048358C (fr) Tole d'acier laminee a chaud pour tube d'intervention enroule
JP5316635B2 (ja) エアバック用鋼管の製造方法
JP2011241465A (ja) 高周波焼入れ用圧延鋼材およびその製造方法
KR20170110650A (ko) 항복 강도 및 구멍 확장성이 개선된 포스트 어닐링된 고인장 강도의 코팅된 강 시트
US20180142319A1 (en) Method for manufacturing high-strength and ductile trip steel

Legal Events

Date Code Title Description
WWE Wipo information: entry into national phase

Ref document number: 2011526332

Country of ref document: JP

121 Ep: the epo has been informed by wipo that ep was designated in this application

Ref document number: 11797816

Country of ref document: EP

Kind code of ref document: A1

NENP Non-entry into the national phase

Ref country code: DE

122 Ep: pct application non-entry in european phase

Ref document number: 11797816

Country of ref document: EP

Kind code of ref document: A1