WO2004104255A1 - エアバックシステム用鋼管とその製造方法 - Google Patents
エアバックシステム用鋼管とその製造方法 Download PDFInfo
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- WO2004104255A1 WO2004104255A1 PCT/JP2004/007228 JP2004007228W WO2004104255A1 WO 2004104255 A1 WO2004104255 A1 WO 2004104255A1 JP 2004007228 W JP2004007228 W JP 2004007228W WO 2004104255 A1 WO2004104255 A1 WO 2004104255A1
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- steel pipe
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- tube
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Classifications
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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
- C21D9/08—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for tubular bodies or pipes
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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
- 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
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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
-
- 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
- C22C38/06—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
- 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
- C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
-
- 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
- C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
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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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
-
- 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
- C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
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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
- C22C38/18—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
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B60—VEHICLES IN GENERAL
- B60R—VEHICLES, VEHICLE FITTINGS, OR VEHICLE PARTS, NOT OTHERWISE PROVIDED FOR
- B60R21/00—Arrangements or fittings on vehicles for protecting or preventing injuries to occupants or pedestrians in case of accidents or other traffic risks
- B60R21/02—Occupant safety arrangements or fittings, e.g. crash pads
- B60R21/16—Inflatable occupant restraints or confinements designed to inflate upon impact or impending impact, e.g. air bags
- B60R21/26—Inflatable occupant restraints or confinements designed to inflate upon impact or impending impact, e.g. air bags characterised by the inflation fluid source or means to control inflation fluid flow
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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
- 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
Definitions
- the present invention relates to a steel pipe having high tensile strength of 1000 MPa or more and high toughness and suitable for an airbag system.
- the invention also relates to a method for producing such a steel pipe.
- the present invention relates to a steel pipe for an airbag system having high strength and high toughness that does not exhibit a brittle fracture even when an internal pressure burst test is performed at a temperature of 140 ° C or even 180 ° C for a thin-walled steel pipe. It relates to a manufacturing method. Background art
- an airbag system which deploys an airbag between the occupant and the occupant with gas or the like before the occupant collides with a steering wheel instrument panel or the like in the event of a collision. It absorbs the kinetic energy of the body to reduce injury.
- the latter type of airbag system holds the deployment gas at high pressure in a steel tube, commonly called an accumulator.
- an accumulator In the event of a collision, the gas in the accumulator is blown out into the airbag at once.
- stress is applied to the steel pipe used as a high-pressure gas accumulator for deployment in a very short time at a large strain rate.
- steel pipes used as accumulators for airbag systems are required to have high dimensional accuracy, workability, and weldability. High strength and excellent burst resistance are also required.
- a steel pipe for an airbag system suitably used for an accumulator and a method for producing the same are described in, for example, JP-A-10-140238, JP-A-10-140249, JP-A-10-140250, JP-A-10-140283, JP-A-10-140283. — 212549, JP-A-2002-294339, JP-A-11-119929, JP-A-2001-49343, and JP-A-2002-194501.
- the technologies described in each of the above publications are intended for high-strength and high-toughness airbag system steel pipes, they aim at a tensile strength of 590 MPa or more. Was only 947 MPa at most.
- the present invention provides a steel pipe suitable for use in a high strength, high toughness airbag system (ie, for an airbag system accumulator).
- the steel pipe can satisfy various characteristics required in the above-mentioned current situation.
- the present invention also provides a method for producing such a steel pipe.
- the steel pipe In order to provide a steel pipe for an airbag system having high tensile strength and excellent burst resistance, which can sufficiently cope with a high accumulator pressure and a thin steel pipe, the steel pipe has the following characteristics. Was found to be necessary.
- burst resistance is important. This is demonstrated by the fact that the crack does not propagate along the entire length of the steel pipe. Such burst resistance is also demonstrated in the internal pressure burst test at -80 ° C. Is more desirable.
- the steel pipe suitable for an air bag system (for Aki Yumure evening formation of air bag system), the mass 0/0, C: 0.05 ⁇ 0.20% , Si: 0.1 ⁇ 1.0%, P : 0.025% or less, S: 0.010% or less, Cr: 0.05 to 1.0%, A1: 0.10% or less, and an amount of ⁇ and / or Mn satisfying the following formulas (1) and (2).
- the balance has a steel composition consisting of iron and impurities (where the symbol of the element means mass% of the element).
- This steel pipe has a tensile strength of 1000 MPa or more.
- the steel composition further contains one or more of Mo: 0.05 to 0.50%, Ni: 0.05 to 1.5%, V: 0.01 to 0.2%, and B: 0.0003 to 0.005%. It is good.
- This steel composition is one of Cu: 0.05-0.5% and Nb: 0.003-0.1%.
- the steel composition may further contain one or more of Ca: 0.0003 to 0.01%, Mg: 0.0003 to 0.01%, and REM: 0.0003 to 0.01%.
- a method of manufacturing a steel pipe for an airbag system includes: forming a steel pipe having a predetermined size from a steel having the above steel composition by a method including pipe making and subsequent cold working; Thereafter, it involves heating the cold-worked steel pipe to a temperature above the Ac, transformation point, then quenching, and then tempering at a temperature below the Ac 1 transformation point.
- the cold worked steel pipe is heated to a temperature of 3 or more Ac, more preferably in the range of 900-1000 ° C.
- This heating is preferably performed by rapid heating at a rate of temperature rise of 10 ° CZ seconds or more, for example, high-frequency induction heating.
- the subsequent quenching is preferably performed at a temperature range of at least 850 to 500 ° C at a cooling rate of 20 ° C / sec or more.
- New it is possible to produce a steel pipe having a fine grain structure with a grain size of 11 or more after quenching (the larger the number, the finer the grain size).
- Such steel pipes exhibit extremely good burst resistance, with no significant crack growth observed even at -80 ° C internal pressure burst tests.
- Each of the above-listed patent publications has a steel composition according to the present invention that satisfies the above formulas (1) and (2), and has a high strength of 1000 MPa or more and 100% ductility at 140 ° C. There is no disclosure of a material that satisfies both the characteristics of high fracture toughness.
- the tensile strength of typical steels disclosed in these patent publications is shown in Fig. 2 in relation to the value of (Mn + 40XTO).
- Fig. 1 is a graph showing the relationship between the tensile strength in the circumferential direction of the steel pipe and vTrslOO, and
- FIG. 2 is a graph showing the relationship between the numerical value of (Mn + 40 ⁇ Ti) and the tensile strength in the circumferential direction of the steel pipe of the steel disclosed in the examples of the present invention and the above-mentioned patent publication. DETAILED DESCRIPTION OF THE INVENTION
- the steel pipe for an airbag system has the specific steel composition described above, and this steel composition has a Ti and ⁇ content satisfying the following equations (1) and (2).
- the content of either Ti or Mn may be 0%.
- Carbon (C) is an element that is inexpensively effective in increasing the strength of steel. If the content is less than 0.05%, it is difficult to obtain a desired tensile strength of 1000 MPa or more, while if it exceeds 0.20%, workability and weldability are reduced. A preferred range of the C content is 0.08 to 0.20%, and a more preferred range is 0.12 to 0.17%.
- Gay element (Si) is an element that not only has a deoxidizing effect, but also enhances the hardenability of steel and improves its strength. In consideration of these effects of Si, the content is set to 0.1% or more. However, if the content exceeds 1.0%, the toughness decreases. The preferable range of the Si content is 0.2 to 0.5%.
- Phosphorus (P) causes a decrease in toughness due to grain boundary bias. In particular, when the content exceeds 0.025%, the toughness is significantly reduced.
- the P content is preferably 0.020% or less, more preferably 0.015% or less.
- Eo (S) decreases the toughness of the steel pipe, especially in the T direction, that is, the circumferential direction of the steel pipe. In particular, if the content exceeds 0.010%, the toughness of the steel pipe in the T direction is significantly reduced.
- the S content is preferably 0.005% or less, and more preferably 0.003% or less.
- Chromium (Cr) is an effective element for increasing the strength and toughness of steel. If the content is less than 0.05%, it is difficult to obtain a strength of 1000 MPa. However, if the content exceeds 1.0%, the toughness of the welded joint is reduced. A preferable range of the Cr content is 0.2 to 0.8%, and a more preferable range is 0.4 to 0.7%.
- A1 0.10% or less
- Aluminum (A1) has a deoxidizing effect and is an effective element for improving toughness and workability. However, if the content of A1 exceeds 0.10%, the occurrence of ground flaws becomes remarkable. Since the A1 content may be at the impurity level, the lower limit is not particularly defined, but is preferably 0.005% or more. The preferred range of the A1 content is 0.005 to 0.05%.
- the A1 content in the present invention refers to the content of acid-soluble A1 (so-called “sol.Al”). Refers to the quantity.
- the content of Mn and Ti must satisfy the above formulas (1) and (2). Adjust as follows.
- Titanium ( ⁇ ) may or may not be added to the steel composition of the present invention.
- the content should be 0.02% or less to satisfy the equation (1).
- the lower limit is not specified and includes the case of impurity level.
- Ti is an element that has a deoxidizing effect when added. In addition, it has a strong affinity for N and is stable as a 'nitride at high temperatures. Therefore, it suppresses crystal grain growth during hot rolling and contributes to improvement in toughness. In order to obtain such an effect, it is preferable that the content of Ti is 0.003% or more. However, if the Ti content exceeds 0.02%, the toughness is rather reduced. Therefore, when Ti is added, the content is preferably set to 0.003 to 0.02%.
- Manganese (Mn) has a deoxidizing effect and is an effective element for improving the hardenability of steel to improve strength and toughness, so it can be contained up to 1.2%. If the content is less than 0.20%, sufficient strength and toughness may not be obtained, so the Mn content is preferably set to 0.20% or more. On the other hand, if the Mn content exceeds 1.0%, MnS becomes coarse and may expand during hot rolling, resulting in a decrease in toughness. Therefore, the content of Mn is preferably 0.20 to 1.0%, more preferably 0.4 to 0.8%.
- the content of Ti and Mn is adjusted so as to satisfy the above formula (If the value of ( ⁇ + 40 ⁇ ) is less than 0.4% or more than 1.2%, desired high strength and / or high toughness can be obtained.
- the value of (Mn + 40xTi) is preferably 0.6% or more and 1.0% or less.
- one of Mo, NCu, V, Nb, B, Ca, Mg and REM may be added to the steel composition of the steel pipe according to the present invention within the range described below. Can be.
- Mo molybdenum
- Ni nickel
- B boron
- V vanadium
- Mo also has the effect of increasing strength through solid solution strengthening and precipitation strengthening. Although the action of Mo can be obtained even when the content is at the impurity level, it is preferable to set the content of Mo to 0.05% or more in order to obtain the effect more remarkably. However, if the Mo content exceeds 0.50%, the weld is hardened and the toughness is reduced. Therefore, the content of Mo when added is preferably 0.05 to 0.50%, more preferably 0.1 to 0.35%.
- Ni also has the effect of further increasing toughness. Although the action of Ni can be obtained even when the content is at the impurity level, in order to obtain the effect more remarkably, it is preferable that the content of ⁇ ⁇ be 0.05% or more. However, ⁇ is an expensive element, and if the content exceeds 1.5%, the cost will increase significantly. Therefore, the content of Ni when added is preferably 0.05 to 1.5%, more preferably 0.1 to 1.0%.
- the content of B is preferably 0.0003% or more.
- the content of B when added is preferably 0.0003 to 0.005%.
- a more preferable range of the B content is 0.0003 to 0.002%.
- V also has the effect of increasing the strength by precipitation strengthening. Such an effect of V is effective when it is contained at 0.01% or more, but when it exceeds 0.2%, toughness is reduced. Therefore, the content of V when added is preferably 0.01% to 0.2%. A more preferable range of the V content is 0.03 to 0.10%.
- the Cu content is preferably set to 0.05% or more, more preferably 0.1%.
- Cu lowers the hot workability of steel. Therefore, when Cu is contained, it is better to include ⁇ to ensure the hot workability. If the Cu content exceeds 0.5%, good hot workability may not be ensured even when Ni is added in combination with Ni. Therefore, the content of Cu when added is preferably 0.05 to 0.5%.
- the Nb content is preferably 0.003% or more, more preferably 0.13%. 005% or more.
- the content of Nb when added is preferably 0.003 to 0.1%.
- the more preferable range of the Nb content is 0.003 to 0.03%, and the still more preferable range is 0.005 to 0.02%.
- calcium (Ca), magnesium (Mg) and rare earth metal elements (REM) must be used. It may be contained as an optional component.
- All of these elements have the effect of improving the anisotropy of toughness and increasing the T-direction toughness of the steel pipe, thereby further improving the burst resistance.
- This effect can be obtained even when the content is at the impurity level, but in order to obtain the effect more remarkably, it is preferable that the content of each element is 0.0003% or more. However, if any of these elements exceeds 0.01%, the inclusions will form a cluster and the problem of ground flaws will occur. Therefore, when these elements are added, the content is preferably 0.0003 to 0.01%, more preferably 0.0005 to 0.003%.
- a seamless steel pipe or a welded pipe is manufactured from steel whose chemical composition is adjusted as described above. From the viewpoint of reliability, a seamless steel pipe is preferable.
- the method for producing seamless steel pipes and welded pipes is not particularly limited.
- the seamless steel pipe or the welded pipe manufactured as described above is cold-worked under conditions selected so as to impart a predetermined dimensional accuracy and surface properties to the steel pipe.
- the method of cold working is not limited as long as predetermined dimensional accuracy and surface properties can be obtained. Examples of useful cold working include cold drawing and cold rolling.
- the working ratio of the cold working does not need to be particularly specified, but it is preferable that the working ratio be 3% or more in terms of a reduction in area.
- An intermediate softening heat treatment may be applied before cold working in order to reduce the working force of cold working.
- the steel pipe is subjected to a heat treatment to ensure the required tensile strength and to increase the T-direction toughness and ensure the burst resistance.
- a high strength of at least 1000 MPa in tensile strength steel pipe, in order to and a ⁇ Baichi strike resistance was quenched after heating to A C l or more variable state point temperature, then, A C l transformation point Perform tempering at the following temperature.
- the heating temperature is preferably set to a temperature equal to or higher than the Ac 3 transformation point in the austenitic region.
- Heating for a long time at high temperature increases the scale generated on the surface of the steel pipe, lowers the dimensional accuracy and surface properties, and lowers the ballasting resistance. After heating, it is preferable to hold for a short time.
- This rapid heating is preferably performed at a heating rate of 10 ° C./sec or more.
- Such rapid heating can be achieved, for example, by high-frequency induction heating or direct current heating, but the heating means is not particularly limited.
- a preferred heating means is high frequency induction heating.
- the preferred heating temperature is in the range of 900-1000 ° C, most preferably in the range of 900-960 ° C. At a lower heating temperature of 900, complete austenitization during brief heating may not be possible, and normal tissue may not be obtained. If the heating temperature exceeds 1000 ° C, the grain size may become coarse and the toughness may decrease.
- the heating atmosphere when heating to a temperature above the Ac, transformation point is preferably an environment with as low an oxygen potential as possible from the viewpoint of suppressing the generation of surface scale. It is more preferable that the atmosphere has an original atmosphere.
- Cooling after heating to a temperature of not less than the Ac i transformation point, preferably not less than the Ac 3 transformation point, is performed by quenching (specifically, 850 to 500) in order to stably and reliably obtain a desired tensile strength of 1000 MPa or more.
- quenching specifically, 850 to 500
- the cooling rate is at least 20 ° C / sec.
- Such rapid cooling can be realized by water quenching or the like.
- Is quenched is cooled to room temperature near the steel pipe is tempered at A C l transformation point temperature to provide the desired 1000 MPa or more tensile strength and ⁇ Baichi strike resistance.
- This tempering does not change the grain size. When the tempering temperature exceeds the Ac, transformation point, it becomes difficult to obtain the above characteristics stably and reliably.
- This tempering is preferably performed by maintaining the temperature in a temperature range of 450 to 700 ° C for 10 minutes or more. After tempering, the bend may be appropriately corrected with a straightener or the like.
- a fixed length was cut out from each steel pipe, and cut at room temperature in the length direction of the pipe to develop.
- a Charpy impact test was performed using a V-notch Charpy test specimen with a width of 2.5 thighs specified in JIS Z 2002 collected from the deployed tube in the T direction.
- a tensile test was performed using a No. 11 test piece specified in JIS Z 2201 sampled from the T direction in accordance with the metal material tensile test method specified in JiS Z2241.
- Table 2 and Fig. 1 show the relationship between the lower limit temperature (hereinafter referred to as vTrslOO) at which the obtained ductile fracture rate of 100% can be obtained and the bow I tensile strength.
- VTrs lOO tended to increase with increasing tensile strength.
- the tensile strength exceeded 1000 MPa, but the vTrs lOO greatly exceeded 140 ° C.
- the tensile strength is not less than 1000 MPa.
- VTrslOO satisfied — 40 ° C.
- the steel pipe finished by cold drawing was heated to 920 ° C in a normal walking beam furnace, held at that temperature for 10 minutes, water quenched, and then, as in Example 1. Heating was performed for 30 minutes at a temperature below the Ac, point for tempering in a normal walking beam furnace.
- Each of the heat-treated steel pipes was subjected to a tensile test, a Charpy impact test, and a burst test.
- the Charpy impact test was performed in the same manner as in Example 1 using a V-notch Charpy test specimen with a specified width of 2.5 mm in JIS Z 2202 taken from the circumferential direction (T direction) of the steel pipe developed at room temperature.
- the toughness was evaluated by vTrs lOO.
- the tensile test was performed according to the metal material tensile test method specified in JIS Z2241, using a No. 11 test piece specified in JIS Z2201 sampled in the same manner as the Charpy test piece.
- a seamless steel pipe having the composition shown in Table 3 was produced in the same manner as in Example 2 except that the heat treatment conditions were changed.
- Example 2 a steel pipe finished by drilling, hot rolling and cold center processing as described in Example 2 was heated at a heating rate of about 20 ° C / sec using a high-frequency induction heating device. Heated to 920 ° C. After the temperature of the tube reached 920 ° C, induction heating was maintained for 5 seconds. Thereafter, water quenching was performed in the same manner as in Example 2, and then heating was performed for 30 minutes for tempering in a normal walking beam furnace.
- Example 2 For each steel pipe, the grain size of the steel was examined by the JIS G0551 Bechet-Beaujard method. The bow I tension and vTrs were measured in the same manner as in Example 2. The internal pressure burst test was performed in the same manner as in Example 1, except that the test was conducted at a temperature of _80 ° C instead of 140 ° C, and evaluated based on the presence or absence of cracks that had propagated to either end of the bursted steel pipe. did. Table 4 also shows these results.
- the steel composition contains Mo, Ni, V, and B
- the hardenability is better than when it is not, so that a homogeneous quenched and tempered structure is easily obtained, and the balance between strength and toughness is excellent, so the toughness is high.
- the strength could be further increased without any decrease.
- FIG. 2 shows, in order to compare the present invention and the prior art, the equation (2) in the example of the present invention and the example satisfying the range of the specific steel composition in the publications disclosed in the above-mentioned patent documents.
- the relationship between the value of ( ⁇ + 40 ⁇ ⁇ ) and the tensile strength was shown.
- the strength can be increased to over 1000 MPa by satisfying the expression (2).
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Abstract
Description
Claims
Priority Applications (5)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
ES04734119.3T ES2605739T3 (es) | 2003-05-21 | 2004-05-20 | Tuberías de acero para sistema de balón de protección y procedimiento para su fabricación |
EP04734119.3A EP1637619B1 (en) | 2003-05-21 | 2004-05-20 | Steel pipe for airbag system and method for its manufacture |
JP2005506406A JP4529901B2 (ja) | 2003-05-21 | 2004-05-20 | エアバッグシステム用鋼管とその製造方法 |
CA002525062A CA2525062C (en) | 2003-05-21 | 2004-05-20 | Steel pipe for an airbag system and a method for its manufacture |
MXPA05012511A MXPA05012511A (es) | 2003-05-21 | 2004-05-20 | Tubo de acero para sistema de bolsa de aire y un metodo para su fabricacion. |
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP2003-143764 | 2003-05-21 | ||
JP2003143764 | 2003-05-21 |
Publications (1)
Publication Number | Publication Date |
---|---|
WO2004104255A1 true WO2004104255A1 (ja) | 2004-12-02 |
Family
ID=33475138
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
PCT/JP2004/007228 WO2004104255A1 (ja) | 2003-05-21 | 2004-05-20 | エアバックシステム用鋼管とその製造方法 |
Country Status (12)
Country | Link |
---|---|
US (2) | US20050000601A1 (ja) |
EP (1) | EP1637619B1 (ja) |
JP (1) | JP4529901B2 (ja) |
KR (1) | KR100711612B1 (ja) |
CN (1) | CN100415922C (ja) |
AR (1) | AR044546A1 (ja) |
CA (1) | CA2525062C (ja) |
ES (1) | ES2605739T3 (ja) |
MX (1) | MXPA05012511A (ja) |
PL (1) | PL1637619T3 (ja) |
TW (1) | TWI243212B (ja) |
WO (1) | WO2004104255A1 (ja) |
Cited By (8)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
WO2007091585A1 (ja) * | 2006-02-09 | 2007-08-16 | Sumitomo Metal Industries, Ltd. | エアバッグインフレータ用ボトル部材の製造方法 |
WO2008050628A1 (fr) * | 2006-10-27 | 2008-05-02 | Sumitomo Metal Industries, Ltd. | Tube en acier sans soudure pour accumulateurs pour air-bag et procédé de fabrication de ceux-ci |
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Cited By (14)
Publication number | Priority date | Publication date | Assignee | Title |
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KR101178954B1 (ko) | 2003-10-10 | 2012-08-31 | 테나리스 커넥션즈 아.게. | 저온에서 초고강도 및 우수한 인성을 가지는 저탄소 합금강철 튜브 및 그것을 제조하는 방법 |
JP5228492B2 (ja) * | 2006-02-09 | 2013-07-03 | 新日鐵住金株式会社 | エアバッグインフレータ用ボトル部材の製造方法 |
KR101008807B1 (ko) | 2006-02-09 | 2011-01-14 | 수미도모 메탈 인더스트리즈, 리미티드 | 에어백 인플레이터용 보틀 부재의 제조 방법 |
WO2007091585A1 (ja) * | 2006-02-09 | 2007-08-16 | Sumitomo Metal Industries, Ltd. | エアバッグインフレータ用ボトル部材の製造方法 |
JP2009532584A (ja) * | 2006-04-03 | 2009-09-10 | テナリス・コネクシヨンズ・アクチエンゲゼルシヤフト | 低温における超高度の強度及び優れた靭性を有する低炭素合金鋼管並びにその製法 |
WO2008050628A1 (fr) * | 2006-10-27 | 2008-05-02 | Sumitomo Metal Industries, Ltd. | Tube en acier sans soudure pour accumulateurs pour air-bag et procédé de fabrication de ceux-ci |
US8496763B2 (en) | 2006-10-27 | 2013-07-30 | Sumitomo Metal Industries, Ltd. | Seamless steel tube for an airbag accumulator and process for its manufacture |
JP5018784B2 (ja) * | 2006-10-27 | 2012-09-05 | 住友金属工業株式会社 | エアバッグアキュムレータ用継目無鋼管とその製造方法 |
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 |
WO2011151908A1 (ja) | 2010-06-03 | 2011-12-08 | 住友金属工業株式会社 | エアバッグ用鋼管とその製造方法 |
JP5234226B2 (ja) * | 2010-06-03 | 2013-07-10 | 新日鐵住金株式会社 | エアバッグ用鋼管の製造方法 |
WO2011152447A1 (ja) * | 2010-06-03 | 2011-12-08 | 住友金属工業株式会社 | エアバッグ用鋼管の製造方法 |
US9080223B2 (en) | 2010-06-03 | 2015-07-14 | Nippon Steel & Sumitomo Metal Corporation | Steel tube for airbags and a process for manufacturing same |
WO2013094116A1 (ja) | 2011-12-21 | 2013-06-27 | 新日鐵住金株式会社 | エアバック用鋼管の製造方法 |
Also Published As
Publication number | Publication date |
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US20060130945A1 (en) | 2006-06-22 |
JP4529901B2 (ja) | 2010-08-25 |
KR100711612B1 (ko) | 2007-04-27 |
AR044546A1 (es) | 2005-09-21 |
MXPA05012511A (es) | 2006-02-08 |
TW200426224A (en) | 2004-12-01 |
ES2605739T3 (es) | 2017-03-16 |
CA2525062C (en) | 2009-08-04 |
KR20060012310A (ko) | 2006-02-07 |
EP1637619A4 (en) | 2008-08-06 |
PL1637619T3 (pl) | 2017-05-31 |
EP1637619A1 (en) | 2006-03-22 |
EP1637619B1 (en) | 2016-11-02 |
JPWO2004104255A1 (ja) | 2006-07-20 |
CN1791694A (zh) | 2006-06-21 |
US20050000601A1 (en) | 2005-01-06 |
CN100415922C (zh) | 2008-09-03 |
US7727463B2 (en) | 2010-06-01 |
CA2525062A1 (en) | 2004-12-02 |
TWI243212B (en) | 2005-11-11 |
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