WO2013175821A1 - 中空スタビライザ並びに中空スタビライザ用鋼管及びその製造方法 - Google Patents
中空スタビライザ並びに中空スタビライザ用鋼管及びその製造方法 Download PDFInfo
- Publication number
- WO2013175821A1 WO2013175821A1 PCT/JP2013/054815 JP2013054815W WO2013175821A1 WO 2013175821 A1 WO2013175821 A1 WO 2013175821A1 JP 2013054815 W JP2013054815 W JP 2013054815W WO 2013175821 A1 WO2013175821 A1 WO 2013175821A1
- Authority
- WO
- WIPO (PCT)
- Prior art keywords
- less
- steel pipe
- hollow stabilizer
- hollow
- content
- Prior art date
Links
Images
Classifications
-
- 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
- C21D9/50—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for welded joints
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21C—MANUFACTURE OF METAL SHEETS, WIRE, RODS, TUBES OR PROFILES, OTHERWISE THAN BY ROLLING; AUXILIARY OPERATIONS USED IN CONNECTION WITH METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL
- B21C37/00—Manufacture of metal sheets, bars, wire, tubes or like semi-manufactured products, not otherwise provided for; Manufacture of tubes of special shape
- B21C37/06—Manufacture of metal sheets, bars, wire, tubes or like semi-manufactured products, not otherwise provided for; Manufacture of tubes of special shape of tubes or metal hoses; Combined procedures for making tubes, e.g. for making multi-wall tubes
- B21C37/08—Making tubes with welded or soldered seams
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21C—MANUFACTURE OF METAL SHEETS, WIRE, RODS, TUBES OR PROFILES, OTHERWISE THAN BY ROLLING; AUXILIARY OPERATIONS USED IN CONNECTION WITH METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL
- B21C51/00—Measuring, gauging, indicating, counting, or marking devices specially adapted for use in the production or manipulation of material in accordance with subclasses B21B - B21F
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B60—VEHICLES IN GENERAL
- B60G—VEHICLE SUSPENSION ARRANGEMENTS
- B60G21/00—Interconnection systems for two or more resiliently-suspended wheels, e.g. for stabilising a vehicle body with respect to acceleration, deceleration or centrifugal forces
- B60G21/02—Interconnection systems for two or more resiliently-suspended wheels, e.g. for stabilising a vehicle body with respect to acceleration, deceleration or centrifugal forces permanently interconnected
- B60G21/04—Interconnection systems for two or more resiliently-suspended wheels, e.g. for stabilising a vehicle body with respect to acceleration, deceleration or centrifugal forces permanently interconnected mechanically
- B60G21/05—Interconnection systems for two or more resiliently-suspended wheels, e.g. for stabilising a vehicle body with respect to acceleration, deceleration or centrifugal forces permanently interconnected mechanically between wheels on the same axle but on different sides of the vehicle, i.e. the left and right wheel suspensions being interconnected
- B60G21/055—Stabiliser bars
-
- 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
- C21D7/00—Modifying the physical properties of iron or steel by deformation
- C21D7/02—Modifying the physical properties of iron or steel by deformation by cold working
- C21D7/04—Modifying the physical properties of iron or steel by deformation by cold working of the surface
- C21D7/06—Modifying the physical properties of iron or steel by deformation by cold working of the surface by shot-peening or the like
-
- 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
- C21D7/00—Modifying the physical properties of iron or steel by deformation
- C21D7/13—Modifying the physical properties of iron or steel by deformation by hot working
-
- 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
-
- 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
- C21D9/08—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
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—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
- C22C38/22—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
-
- 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
- C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
-
- 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
-
- 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
- C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
-
- 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
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B60—VEHICLES IN GENERAL
- B60G—VEHICLE SUSPENSION ARRANGEMENTS
- B60G2206/00—Indexing codes related to the manufacturing of suspensions: constructional features, the materials used, procedures or tools
- B60G2206/01—Constructional features of suspension elements, e.g. arms, dampers, springs
- B60G2206/40—Constructional features of dampers and/or springs
- B60G2206/42—Springs
- B60G2206/427—Stabiliser bars or tubes
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B60—VEHICLES IN GENERAL
- B60G—VEHICLE SUSPENSION ARRANGEMENTS
- B60G2206/00—Indexing codes related to the manufacturing of suspensions: constructional features, the materials used, procedures or tools
- B60G2206/01—Constructional features of suspension elements, e.g. arms, dampers, springs
- B60G2206/70—Materials used in suspensions
- B60G2206/72—Steel
-
- 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
- C21D2211/004—Dispersions; Precipitations
-
- 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
- C21D2211/005—Ferrite
-
- 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
-
- 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
- C21D2211/009—Pearlite
Definitions
- the present invention relates to a hollow stabilizer used in a vehicle such as an automobile, a steel pipe for a hollow stabilizer which is a material thereof, and a method for manufacturing the same.
- Vehicles such as automobiles employ a stabilizer that relaxes rolling of the body during cornering and ensures the stability of the body during high-speed driving.
- stabilizers were manufactured by processing solid materials such as steel bars into the required shape, but in recent years, hollow materials such as seamless steel pipes and ERW welded steel pipes have been used to reduce weight. The number of hollow stabilizers has increased.
- the outer diameter of the hollow stabilizer must be larger than that of the solid stabilizer in order to maintain the same roll rigidity.
- the generated stress for the same load is higher in the hollow stabilizer, and it is necessary to increase the thickness / outer diameter ratio (t / D) to suppress the increase in the generated stress.
- the hollow stabilizer may cause fatigue failure from the inner surface that does not exist in the solid stabilizer. This is because even if the fatigue strength of the outer surface is improved by increasing the strength of the steel pipe, the decarburized layer on the inner surface serves as a starting point for fatigue failure.
- a steel pipe for a hollow stabilizer in which t / D is set to 0.20 or more and generation of a decarburized layer on the inner surface is suppressed has been proposed (for example, Patent Document 3).
- FIG. 1A is a perspective view of an electric resistance welded pipe
- FIG. 1B is a base material when the electric resistance welded pipe 16 surrounded by a circle S1 in FIG.
- FIG. 1C is an enlarged view of the metal flow 18 of the welded portion 19 in a cross-sectional view of the ERW weld pipe 16 surrounded by the circle S2 of FIG. 1A.
- FIG. 1 (d) is an enlarged view showing the presence state of MnS when the electric resistance welding contact portion of the electric resistance welding pipe 16 is viewed in a longitudinal section along the extending direction (L direction).
- L direction extending direction
- FIG. 1B and FIG. 1C The metal flow 18 in which the central segregation zone of the steel sheet is perpendicular to the thickness direction is formed by the upset of the butted surfaces. Therefore, when MnS20 stretched in the longitudinal direction by rolling is present in the central segregation zone of the steel plate, the surface in the vicinity of the ERW weld 19 after the weld bead is cut is shown in FIG. Such stretched MnS20 is present, and becomes a starting point of fatigue fracture.
- An object of the present invention is to provide a hollow stabilizer that has higher strength and excellent fatigue characteristics than the conventional art and a steel pipe for a hollow stabilizer that is a material for the hollow stabilizer. .
- the hollow stabilizer is manufactured by quenching and tempering in order to adjust the material.
- the hardenability is ensured by the addition of Cr.
- Mn, S, Ca, and O it is necessary to limit Mn, S, Ca, and O in order to prevent deterioration of fatigue strength due to MnS in the vicinity of the ERW weld.
- t / D and the thickness of the decarburized layer are limited to prevent fatigue fracture from the inner surface, and more preferably, compressive residual stress is applied by shot peening.
- the gist of the present invention is as follows.
- the component composition is such that the critical cooling rate Vc90 represented by (Equation 1) is 40 ° C./s or less, and the metal structure is from a mixed structure of ferrite and pearlite.
- the length of the stretched MnS present in the thickness center is 150 ⁇ m or less, the Rockwell B scale hardness (HRB) is 95 or less, and the thickness / outer diameter ratio is 0.14 or more.
- the steel pipe is an electric resistance steel pipe and is heated to 800 to 1200 ° C. after electric resistance welding, and the cross-section reduction rate is 40 to 80%.
- the manufacturing method of the steel pipe for hollow stabilizers characterized by including the process of carrying out diameter reduction rolling hot so that it may become the range of this.
- FIG. 1 (a) to 1 (c) are diagrams for explaining the relationship between the surface layer of the ERW weld and the MnS of the center segregation zone, where FIG. 1 (A) is the ERW welded pipe, FIG. 1 (B). Is an enlarged view of the metal flow of the base metal part when the electric resistance welded pipe surrounded by the circle S1 in FIG. 1 (a) is viewed in cross section, and FIG. 1 (c) is the circle S2 in FIG. 1 (a).
- Fig. 1 (d) is an enlarged view of the metal flow of the welded portion as seen in a cross section of the electric resistance welded pipe enclosed by It is an enlarged view when it sees with the longitudinal cross-section in alignment with a direction.
- FIG. 1 (A) is the ERW welded pipe
- FIG. 1 (B) Is an enlarged view of the metal flow of the base metal part when the electric resistance welded pipe surrounded by the circle S1 in FIG. 1 (a) is viewed in cross
- FIG. 2 is a diagram illustrating an example of a stabilizer.
- 3 (a) and 3 (b) are diagrams for explaining a method of producing a flat bending fatigue test piece flat plate from an electric resistance welded pipe, and FIG. 3 (a) is a longitudinal direction of the electric resistance welded pipe. It is a perspective view which shows the state after making a notch
- 4 (a) and 4 (b) are diagrams for explaining a plane bending fatigue test piece manufactured using the flat plate of FIG. 3 (b).
- FIG. 4 (a) is a plan view
- FIG. b) is a side view.
- FIG. 5 (a) and 5 (b) show the fracture surface of the test piece after the fatigue test.
- FIG. 5 (a) is an SEM photograph when the fracture surface of the test piece is observed
- FIG. b) is an EDX analysis result performed at a position surrounded by an ellipse of a fracture surface shown in FIG.
- FIG. 6 is a photograph showing a metal flow in a cross section perpendicular to the fracture surface of the test piece after the fatigue test, and the photos are pasted together at the fracture surface position.
- the stabilizer 10 includes a torsion part 11 that extends in the width direction of the vehicle body (not shown), and a pair of left and right arm parts 12 that are continuous from the torsion part 11 to both ends.
- the torsion part 11 is fixed to the vehicle body side via a bush 14 or the like.
- the terminal 12a of the arm unit 12 is connected to the left and right suspension mechanisms 15 via a stabilizer link (not shown).
- the torsion part 11 and the arm part 12 are usually bent at several or a dozen places for the purpose of avoiding interference with other parts.
- the suspension mechanism 15 receives an input of upside down phase.
- the left and right arm portions 12 bend in the opposite direction, and the torsion As a result of the portion 11 being twisted, it functions as a spring that suppresses excessive tilting (rolling) of the vehicle body, and repeats straight traveling and turning while the vehicle is traveling. Therefore, the stabilizer is required to have hardness and fatigue characteristics.
- the HRC50 is set as the upper limit as the achievable hardness
- the substantial upper limit value HRC40 of the conventional material is set as the lower limit. did.
- the thickness / outer diameter ratio t / D of the hollow stabilizer of the present invention is set to 0.14 or more so that the starting point of fatigue failure is the outer surface. That is, if t / D is smaller than 0.14, the difference in stress between the outer surface and the inner surface is small, and fatigue tends to occur from the inner surface where it is difficult to find a preexisting fatigue starting point.
- the upper limit of t / D is not particularly limited. However, since t / D is theoretically solid at 0.5, the upper limit of t / D of the present invention is substantially less than 0.5. From a practical point of view, when t / D is 0.25 or more, the effect of reducing the weight is reduced and the manufacturing becomes difficult. Therefore, it is preferable to make t / D less than 0.25.
- HRC and t / D are those parts that are not subjected to bending when the hollow stabilizer is manufactured.
- the stretched MnS may become the starting point of fatigue failure.
- the inventors produced a flat bending fatigue test piece flat plate 22 from an electric resistance welded pipe 21, and FIGS. 4 (a) and 4 (b).
- the ERW welded portion 23 of the ERW steel pipe 21 is arranged at a position in the longitudinal center portion of the fatigue test piece 24 and extending in a direction perpendicular to the longitudinal direction of the test piece 24.
- a plane bending fatigue test was performed using the test piece 24.
- the fracture surface of the specimen 24 is observed with a scanning electron microscope (SEM), and the inclusions present at the starting point of fatigue fracture are observed using an energy dispersive X-ray analyzer (EDS) attached to the SEM.
- SEM scanning electron microscope
- EDS energy dispersive X-ray analyzer
- FIGS. 5 (a) and 5 (b) it was confirmed that MnS was present at the fracture starting point of the fractured test piece.
- FIG. 6 the result of observing the metal flow in the cross section perpendicular to the fracture surface of the test piece after the fatigue test is shown in FIG. From FIG. 6, it can be seen that the fracture surface position of the test piece is not a welded part but a position somewhat deviated from the welded part position. Moreover, it confirmed that the surface of the both-sides vicinity part which pinches
- the length of the stretched MnS present at the center of the wall thickness is 150 ⁇ m or less. This is because if the length of the stretched MnS exceeds 150 ⁇ m, it becomes a starting point for fatigue fracture of the ERW weld.
- the presence or absence of MnS exceeding 150 ⁇ m in length was determined by cutting out a 10 mm length in the longitudinal direction from a hollow stabilizer, collecting a cross-sectional tissue test piece, and measuring the optical thickness at the center of the thickness in the cross section of the test piece.
- the length of MnS is confirmed with a microscope.
- the presence of MnS may be confirmed by using a scanning electron microscope observation and energy dispersive X-ray spectroscopy in combination.
- the length of MnS is, for each of ten test pieces, the thickness central portion in the cross section is observed with an optical microscope or a scanning electron microscope, and among the MnS present in the observed region, The length of MnS having the largest dimension is measured.
- the decarburized layer depth of the inner surface portion is set to 20 ⁇ m or less from the inner surface.
- the decarburized layer has a lower strength than the base metal and is likely to be the starting point of fatigue fracture, so it is desirable that the decarburized layer does not exist.
- t / D is 0.14 or more
- the decarburized layer is 20 ⁇ m or less, so It is possible to prevent the occurrence of fatigue fracture.
- the decarburized layer is defined as the maximum depth from the inner surface of the ferrite existing on the inner surface in the hollow stabilizer of the present invention that should have a tempered martensite structure.
- the ferrite grain size of the inner surface of the stabilizer steel pipe before quenching is about 10 to 20 ⁇ m, and when the width corresponding to the grain size of the ferrite grains continuously present on the inner surface is regarded as a layer, If it is suppressed to the dimension of one layer, the ferrite decarburized layer of the steel pipe can be made 20 ⁇ m or less. In order to suppress the occurrence of the decarburized layer, it is preferable to lower the temperature of the inner surface during quenching, shorten the holding time, and increase the cooling rate. By appropriately selecting the quenching conditions when manufacturing the hollow stabilizer, the decarburized layer depth can be set to 20 ⁇ m or less.
- the decarburized layer is formed in a two-phase region that is being cooled from high temperature to room temperature.
- the two-phase region is a temperature range below the Ar 3 transformation temperature at which transformation from austenite to ferrite starts and where austenite and ferrite coexist.
- the fatigue strength is improved, and when the maximum compressive residual stress of the outer surface is 400 MPa or more, the effect becomes remarkable.
- produces is low compared with an outer surface on the inner surface of a hollow stabilizer, it is preferable to give a compressive residual stress also to an inner surface depending on the case depending on the case.
- the method for applying the residual stress is not particularly limited, but shot peening is easiest. Residual stress can be determined by X-ray diffraction.
- C is an element that determines the strength of the hollow stabilizer.
- the C content needs to be 0.26% or more.
- the upper limit of the C content is set to 0.30%.
- the Si is a deoxidizing element and contributes to solid solution strengthening. Furthermore, there exists an effect which raises temper softening resistance, and in order to acquire those effects, it is necessary to contain 0.05% or more, but when it contains exceeding 0.35%, toughness will fall. Therefore, the Si content is set in the range of 0.05 to 0.35%. Preferably, the lower limit of the Si content is 0.20% and the upper limit is 0.30%.
- Mn is an element that improves the hardenability. If the Mn content is less than 0.5%, the effect of improving the hardenability cannot be sufficiently ensured, and if it exceeds 1.0%, delayed fracture occurs. As the properties deteriorate, MnS tends to precipitate and the fatigue strength in the vicinity of the ERW weld is reduced, so the Mn content is in the range of 0.5 to 1.0%, preferably 0.5% or more Less than 0.8%.
- P is an element that adversely affects weld cracking resistance and toughness, it is limited to 0.05% or less. In addition, Preferably, it is 0.03% or less.
- the S content is limited to less than 0.0030%, preferably 0.0026% or less.
- the MnS in order to suppress the precipitation of MnS, it is necessary to suppress not only the S content but also the relationship with the Mn content, specifically, the Mn content and the S content. Is limited to 0.0025 or less. That is, even if the Mn and S contents satisfy the above appropriate range, if the value of the product of the Mn content and the S content exceeds 0.0025, the fatigue strength near the ERW weld is sufficiently obtained. Because it disappears.
- Cr is an element that improves hardenability. If the Cr content is less than 0.05%, these actions and effects cannot be sufficiently expected, and if the Cr content exceeds 1.0%, defects are likely to occur during ERW welding. Therefore, the Cr content is in the range of 0.05 to 1.0%.
- Al is an element useful as a deoxidizer for molten steel, and it is preferable to add 0.01% or more.
- Al is an element that fixes N, the amount of Al greatly affects the crystal grain size and mechanical properties. If the Al content exceeds 0.08%, nonmetallic inclusions increase and surface defects are likely to occur in the product. Therefore, the Al content is set to 0.08% or less.
- the Al content is preferably 0.05% or less, more preferably 0.03% or less.
- Ti acts to stably and effectively improve the hardenability by adding B by fixing N in steel as TiN and suppressing precipitation of BN. Therefore, in order to meet the stoichiometry of TiN, it is necessary to add at least 3.42 times the N content, and the Ti content range is automatically determined from the N content range. However, since there is a portion that precipitates as carbides, in order to ensure the fixation of N, the range of 0.005 to 0.05%, which is higher than the theoretical value, is set. Preferably, the content is 0.01 to 0.02%.
- B is an element that greatly improves the hardenability of steel by adding a small amount.
- the B content is less than 0.0005%, the effect of improving the hardenability cannot be expected.
- the B content exceeds 0.005%, a coarse B-containing phase tends to be generated, and embrittlement occurs. It becomes easy. Therefore, the B content is set to 0.0005% to 0.005%.
- the B content is preferably 0.001 to 0.002%.
- N is an element that has the effect of increasing the strength by precipitating nitride or carbonitride.
- the hardenability decreases due to the precipitation of BN, and as described above, the Ti added to prevent the precipitation of BN causes a decrease in hot workability and fatigue strength due to the precipitation of TiN.
- a decrease in toughness becomes a problem.
- TiN also has the effect of suppressing the coarsening of the ⁇ grain size at high temperatures and improving the toughness. Therefore, in order to optimize the balance of hot workability, fatigue strength, and toughness, the N content is set to 0.006% or less.
- the N content is preferably 0.001 to 0.005%, more preferably 0.002 to 0.004%.
- Ca is an element that has an effect of improving the toughness by fixing S as CaS and preventing a decrease in fatigue strength in the vicinity of the ERW weld due to MnS. If the Ca content is less than 0.0005%, these effects cannot be sufficiently expected. On the other hand, if the Ca content exceeds 0.005%, the amount of oxide in the steel increases and the toughness deteriorates. The range is 0005 to 0.005%.
- the hollow stabilizer of the present invention has the above component composition as an essential component composition, but can further contain Mo, Nb, V, and Ni as necessary.
- Mo is an element that has the effect of improving hardenability. If the Mo content is less than 0.05%, these effects cannot be sufficiently expected. On the other hand, if the Mo content exceeds 0.5%, the alloy cost increases. The range is 0.5%.
- Nb has the effect of improving the toughness by refining the crystal grain size of the steel material in addition to the effect of precipitation strengthening by Nb carbonitride. If the Nb content is less than 0.01%, the effect of improving the strength and toughness is not sufficient, but even if the Nb content exceeds 0.1%, no further improvement effect can be expected, The Nb content is in the range of 0.01 to 0.1% because it only increases the cost.
- V is an element having an effect of precipitation strengthening by V carbonitride. If the V content is less than 0.01%, these effects cannot be sufficiently expected. On the other hand, if the V content exceeds 0.1%, no further improvement effect can be expected, resulting in an increase in alloy costs. Therefore, the V content is in the range of 0.01 to 0.1%.
- Ni is an element having an effect of improving hardenability and toughness. If the Ni content is less than 0.1%, the effect cannot be expected. On the other hand, if the Ni content exceeds 1%, the alloy cost increases, so the Ni content is in the range of 0.1 to 1.0%. And
- the hardenability index examples include iron and steel, 74 (1988) P.I.
- a critical cooling rate Vc90 (° C./s), which is conventionally known from 1073, may be used. This is an index represented by the following (formula 1), and means a cooling rate at which the volume ratio of martensite is 90% or more. Therefore, the lower the Vc90, the higher the hardenability and the martensitic structure can be obtained even when the cooling rate is slow.
- the present inventors manufactured ERW steel pipes having various components, and investigated the relationship between Vc90 and hardness after quenching. As a result, when Vc90 is 40 ° C./s or less, the knowledge that a martensite structure can be surely obtained up to the inner surface by water quenching was obtained. Therefore, in the present invention, the upper limit of Vc90 is 40 ° C./s. .
- the present inventors have 0.30% C, 0.30% Si, 0.35% Cr, steel No. 1 shown in Table 1, Vc90 is 27.1 ° C./s.
- the relationship between the cooling rate and the Rockwell C hardness at the center of the wall thickness was investigated using an electric resistance steel pipe. Rockwell C hardness (HRC) was measured according to JIS Z 2245.
- the metal structure of the hollow stabilizer of the present invention was limited to tempered martensite. The reason is that there is little variation in structure and hardness, and the hardness can be easily adjusted. In order to reliably obtain a martensite structure up to the inner surface by quenching, the hardenability of the material is sufficiently ensured by setting Vc90 to 40 ° C./s or less. It can be observed with an optical microscope that the metal structure of the hollow stabilizer is tempered martensite.
- the metal structure of the steel tube for hollow stabilizer used as the material for the hollow stabilizer of the present invention is preferably composed of a mixed structure of ferrite and pearlite. It can be observed with an optical microscope that the metal structure of the steel tube for a hollow stabilizer is a mixed structure of ferrite and pearlite.
- the hollow stabilizer is often manufactured by bending a steel pipe in the cold, and in order to ensure sufficient workability, the Rockwell B scale hardness (HRB) is desirably 95 or less. By making the metal structure a mixed structure of ferrite and pearlite, workability can be ensured.
- the hardness (HRB) of Rockwell B scale of a steel pipe for a hollow stabilizer can be measured according to JIS Z 2245.
- the depth of the ferrite decarburized layer on the inner surface of the steel pipe for a hollow stabilizer of the present invention is 20 ⁇ m or less. Thereby, the decarburization layer depth of the inner surface of the hollow stabilizer after quenching can be suppressed to within 20 ⁇ m.
- the ferrite decarburization depth means that when the metal structure of the longitudinal section (L section) of the steel pipe is observed with an optical microscope, no cementite is present in the L direction and only ferrite grains are measured from the inner surface. The maximum depth of the lined area.
- the decarburized layer on the inner surface of the steel pipe for a hollow stabilizer is formed, for example, in a two-phase region in the course of being cooled to room temperature after hot-reducing the ERW welded steel pipe.
- a decarburized layer is easily formed on the inner surface of the steel pipe for a hollow stabilizer.
- the amount of C that is an austenite stabilizing element decreases, and the metal structure becomes ferrite.
- the inner surface of the steel pipe for a hollow stabilizer is applied.
- the depth of the generated decarburized layer can be suppressed to 20 ⁇ m or less.
- it may cool by supplying water only from the outer surface of the steel pipe for hollow stabilizers, it is also possible to cool by supplying water also to the inner surface. By increasing the cooling rate of the inner surface of the steel pipe for a hollow stabilizer, the depth of the decarburized layer can be made shallower.
- the manufacturing method of the steel pipe for hollow stabilizers of the present invention will be described. First, molten steel melted to have the required chemical composition is cast into a slab, or once made into a steel ingot, and then hot-rolled into a steel slab. This slab or steel slab is heated. Hot-rolled steel sheet is obtained by hot rolling. This hot-rolled steel sheet is made into an electric-welded steel pipe by a normal method for producing an electric-welded steel pipe, for example, hot or cold electric resistance welding or high-frequency induction heating welding. Further, a thick steel pipe may be manufactured by subjecting this to hot diameter reduction rolling.
- Reduction rolling can be performed using a stretch reducer or the like.
- the stretch reducer is a rolling device provided with a plurality of rolling stands having three or four rolls around the rolling shaft and in series with the rolling shaft, and adjusts the roll rotation speed and the rolling force of each rolling stand of this rolling device. By doing this, it is possible to perform reduction rolling that controls the tension in the tube axis direction (rolling direction) and the compressive force in the circumferential direction of the steel pipe, thereby increasing the thickness / outer diameter ratio.
- the outer diameter is reduced by the rolling force of the outer diameter of the steel pipe while the wall thickness is increased, but on the other hand, the wall thickness is decreased by the tension acting in the tube axis direction of the steel pipe.
- the final wall thickness is determined by the balance. Since the thickness of the steel pipe subjected to diameter reduction rolling is mainly determined by the tension between the rolling stands, the tension between the rolling stands for obtaining the target thickness is obtained from the rolling theory, and the tension works. Thus, it is necessary to set the number of roll rotations of each rolling stand.
- the diameter reduction rolling is preferably performed by heating the ERW steel pipe to 800 to 1200 ° C. and reducing the cross section by 40 to 80%. It is desirable that the steel pipe for hollow stabilizer is an electric resistance welded tube that has been hot-diameter-reduced, but is not limited to this. A drawn tube may be used.
- stabilizer production example 1 Cold Forming Next, stabilizer production example 1 will be described with reference to FIG. A steel pipe cut into a predetermined length (electrically welded pipe, seamless pipe, hot reduced diameter pipe, and these drawn pipes) is bent into the desired shape shown in FIG. 2 (process: bending), furnace heating, Or it heats to an austenite temperature range using an electrical heating or a high frequency heating apparatus (process: heating), and quenches in water (or other quenching medium) (process: quenching). Further, the thermally deformed stabilizer bar is corrected to a desired stabilizer shape (process: shape correction), tempered (process: tempered), and only the outer surface of the tempered pipe or both the outer surface and the inner surface are shot peened. (Process: shot peening) and painted using a desired paint (process: painting). If restraint quenching is performed, shape correction (process: shape correction) can be omitted.
- shape correction process: shape correction
- the heating temperature is preferably 900 ° C. or higher, more preferably 950 ° C. or higher.
- the tempering temperature is determined based on the temper softening curve of the hollow stabilizer steel pipe.
- FIG. 10 shows an electric resistance welded steel pipe containing 0.30% C, 0.30% Si, and 0.35% Cr, steel No. 1 shown in Table 1, with Vc90 of 27.1 ° C. A tempering softening curve is shown. From the temper softening curve shown in FIG. 9, the tempering temperature at which the Rockwell C hardness (HRC) becomes 40 to 50 can be determined.
- HRC Rockwell C hardness
- Each steel type having the composition shown in Table 1 is melted and cast into a slab, and the resulting slab is heated to 1200 ° C and hot-rolled at a hot finishing temperature of 890 ° C and a winding temperature of 630 ° C.
- a steel plate having a thickness of 5 mm was used. These steel sheets were cut to a predetermined width, roll-formed into a tubular shape, and then an electric resistance steel pipe having an outer diameter of 90 mm was manufactured by high frequency electric resistance welding. Furthermore, the obtained ERW steel pipe was heated to 980 ° C.
- the metal structure of the obtained hollow stabilizer steel pipe was observed with an optical microscope, and the metal structures of all the hollow stabilizer steel pipes were a mixed structure of ferrite and pearlite, and the decarburized layer depth on the inner surface was 15 ⁇ m or less. confirmed. Moreover, as a result of measuring Rockwell hardness based on JISZ2245, the Rockwell hardness of all the steel pipes for hollow stabilizers was 95 or less in B scale (HRB). Furthermore, as a result of confirming the presence or absence of MnS exceeding 150 ⁇ m in length using an optical microscope, SEM and EDS in combination, as shown in Table 2, Comparative Example No. In H to K, MnS having a length exceeding 150 ⁇ m was present.
- FIGS. 3 (a) and 3 (b) from the plate-shaped piece developed by cutting into the hollow stabilizer steel pipe at a position of 180 ° from the ERW welded portion, FIG. 4 (a). And the plane bending fatigue test piece whose longitudinal direction center part becomes an ERW weld part as shown to (b) was produced. Similarly, a plane bending fatigue test piece having a center part in the longitudinal direction serving as a base material part was produced from a plate-like piece developed by cutting at the position of the ERW weld. The central part of the test piece in the longitudinal direction had a thickness ta: 3 mm and a width Wa: 15 mm.
- Each test piece was tempered based on a temper softening curve so that the Rockwell hardness was 40 on a C scale (HRC), and a plane bending fatigue test was conducted with a fatigue limit of 5 million times.
- the test results are shown in Table 2.
- the tempering holding time was 30 minutes.
- L to O the difference in fatigue limit between the base metal part and the ERW welded part is as large as 140 MPa or more, and the fatigue characteristics of the ERW welded part are significantly inferior to those of the base metal part.
- the fracture surface after the plane bending fatigue test was observed with an SEM, and the composition of inclusions present at the fatigue fracture starting point was analyzed using the EDS attached to the SEM.
- L to O in the comparative example which is an ERW weld
- the presence of MnS was confirmed at the fracture starting point.
- each steel pipe was cut into a length of 1000 mm, and then bent at 90 ° at a position 200 mm from both pipe ends to form a U shape. Mold. At this time, the portion of the molded U-shaped tube that is visible when viewed in the U-shaped direction, that is, along the side surface of the U-shaped tube, is molded so that the electric-welded welded portion is positioned.
- Test materials a to v were obtained. Thereafter, the test materials an to n (excluding the test material c) as examples of the present invention were heated to 950 ° C. for 10 minutes and water-quenched, and then tempered at 200 ° C. for 30 minutes to adjust the hardness to HRC49.
- test material c after heating at 950 degreeC for 10 minutes and water quenching, it tempered at 350 degreeC for 30 minutes and adjusted the hardness to HRC43. Further, all the test materials a to v were subjected to shot peening processing with a compressive residual stress of 450 MPa on the outer surface after the heat treatment. Further, for the test materials b and f, shot peening was performed on the inner surface so that the compressive residual stress was 450 MPa.
- test materials r and s were produced using the comparative steel (steel 12 of Table 1) which has the typical component composition of the conventionally used hollow stabilizer as a raw material, C content in steel Therefore, the test material r was adjusted to HRC47 which is the upper limit of the obtained hardness, and the test material s was adjusted to HRC40 which is the upper limit of the actually used hardness.
- steel 1 which is a compatible steel shown in Table 1 is used as a raw material, but the test material o having a decarburized layer depth of 25 ⁇ m at the inner surface portion, and the thickness / outer diameter ratio is 0.13.
- a test material p and a test material q having a bainite structure of HRC35 with a cooling rate of 15 ° C./s slower than the case of water quenching were also prepared.
- test material o having a decarburized layer depth of more than 20 ⁇ m on the inner surface portion and the test material p having a small t / D of 0.13 have a larger number of inner surface breakage and the durability standard is 500,000 times. Sometimes it did not reach.
- test material q having a metal structure of bainite and a hardness as low as HRC35 had a significantly low fatigue durability.
- test materials rv which are comparative examples manufactured using comparative steels all have MnS exceeding 150 ⁇ m in length in the steel, two or more of the 20 are electro-welded on the outer surface. There was a case where it broke early from the vicinity of the part.
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Organic Chemistry (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Crystallography & Structural Chemistry (AREA)
- Thermal Sciences (AREA)
- Physics & Mathematics (AREA)
- Manufacturing & Machinery (AREA)
- Heat Treatment Of Articles (AREA)
- Vehicle Body Suspensions (AREA)
- Heat Treatment Of Steel (AREA)
- Metal Extraction Processes (AREA)
Abstract
Description
本発明の要旨は以下のとおりである。
logVc90=2.94-0.75β ・・・ (式1)
ただし、β=2.7C+0.4Si+Mn+0.8Crである。
logVc90=2.94-0.75β ・・・ (式1)
ただし、β=2.7C+0.4Si+Mn+0.8Cr+2.0Mo+0.8Niである。
図2に示すように、スタビライザ10は、図示しない車体の幅方向に延び出すトーション部11と、トーション部11から両端に連続する左右一対のアーム部12とを有している。トーション部11はブッシュ14などを介して車体側に固定されている。アーム部12の端末12aは、左右のサスペンション機構15にスタビライザリンク(図示せず)などを介して連結される。トーション部11およびアーム部12は他の部品との干渉を避ける目的で通常の場合は数個所もしくは十数箇所の曲げ加工がなされている。
本発明の中空スタビライザは、上記成分組成を必須の成分組成とするが、必要に応じて、さらに、Mo、Nb、VおよびNiを含有させることができる。
ただし、β=2.7C+0.4Si+Mn+0.8Cr+2.0Mo+0.8Niである。
次に図8を用いてスタビライザの製造例1を説明する。所定の長さに切断した鋼管(電縫管、シームレス管、熱間縮径管、またこれらの引抜管)を図2に示す所望の形状に曲げ成形し(工程:曲げ成形)、炉加熱、あるいは通電加熱または高周波加熱装置を用いてオーステナイト温度域まで加熱し(工程:加熱)、水中(又は他の焼入れ媒体)に焼入れする(工程:焼き入れ)。更に、熱変形したスタビライザバーを所望のスタビライザ形状に矯正し(工程:形状矯正)、焼戻し処理を施し(工程:焼戻し)、この焼き戻した管の外面のみ、又は外面及び内面の双方をショットピーニングし(工程:ショットピーニング)、所望の塗料を用いて塗装した(工程:塗装)。なお、拘束焼入れを行えば形状矯正(工程:形状矯正を)は省略することが可能である。
次に図9を用いてスタビライザの製造例2を説明する。所定の長さに切断した鋼管(電縫管、シームレス管、熱間縮径管、またこれらの引抜管)を炉加熱、あるいは通電加熱または高周波加熱装置を用いてオーステナイト温度域まで加熱し(工程:加熱)、図2に示す所望の形状に曲げ成形し(工程:曲げ成形)、水中(又は他の焼入れ媒体)に焼入れし(工程:焼き入れ)する。更に、熱変形したスタビライザバーを所望のスタビライザ形状に矯正し(工程:形状矯正)、焼戻し処理を施し(工程:焼き戻し)、この焼き戻した管の外面のみ、又は外面及び内面の双方をショットピーニングし(工程:ショットピーニング)、所望の塗料を用いて塗装した(工程:塗装)。なお、拘束焼入れを行えば形状矯正(工程:形状矯正)は省略することが可能である。
11 トーション部
12 アーム部
12a (アーム部の)端末
14 ブッシュ
15 サスペンション機構
16 電縫溶接管
17 母材部
18 メタルフロー
19 溶接部
20 MnS
21 電縫溶接管
22 平面曲げ疲労試験片用平板
23 電縫溶接部
24 疲労試験片
Claims (7)
- 化学成分として、質量%で、
C:0.26~0.30%、
Si:0.05~0.35%、
Mn:0.5~1.0%、
Cr:0.05~1.0%、
Ti:0.005~0.05%、
B:0.0005~0.005%、
Ca:0.0005~0.005%
を含有し、
Al:0.08%以下、
P:0.05%以下、
S:0.0030%未満、
N:0.006%以下、
O:0.004%以下
に制限し、残部がFe及び不可避的不純物からなり、Mn含有量とS含有量の積の値が0.0025以下であり、(式1)で表される臨界冷却速度Vc90が40℃/s以下となる成分組成を有し、金属組織が焼戻しマルテンサイトからなり、肉厚中央部に存在する延伸したMnSの長さが150μm以下であり、ロックウェルCスケールの硬さ(HRC)が40~50、肉厚/外径比が0.14以上であり、内表面部の脱炭層深さが、内表面から20μm以下であることを特徴とする中空スタビライザ。
logVc90=2.94-0.75β ・・・ (式1)
ただし、β=2.7C+0.4Si+Mn+0.8Crである。 - 質量%で、さらに、
Mo:0.05~0.5%、
Nb:0.01~0.1%、
V:0.01~0.1%、
Ni:0.1~1.0%の1種または2種以上を含有し、(式1)中のβを、β=2.7C+0.4Si+Mn+0.8Cr+2.0Mo+0.8Niとすることを特徴とする請求項1に記載の中空スタビライザ。 - 外表面の最大圧縮残留応力が400MPa以上であることを特徴とする請求項1または2に記載の中空スタビライザ。
- 外表面および内表面に、ショットピーニング加工が施されてなることを特徴とする請求項4に記載の中空スタビライザ。
- 請求項1~5の何れか1項に記載の中空スタビライザの素材として用いられる中空スタビライザ用鋼管であって、
化学成分として、質量%で、
C:0.26~0.30%、
Si:0.05~0.35%、
Mn:0.5~1.0%、
Cr:0.05~1.0%、
Ti:0.005~0.05%、
B:0.0005~0.005%、
Ca:0.0005~0.005%
を含有し、
Al:0.08%以下、
P:0.05%以下、
S:0.0030%未満、
N:0.006%以下、
O:0.004%以下
に制限し、
さらに、必要に応じて、
Mo:0.05~0.5%、
Nb:0.01~0.1%、
V:0.01~0.1%、
Ni:0.1~1.0%の1種または2種以上を含有し、残部がFe及び不可避的不純物からなり、Mn含有量とS含有量の積の値が0.0025以下であり、(式1)で表される臨界冷却速度Vc90が40℃/s以下となる成分組成を有し、金属組織がフェライトとパーライトの混合組織からなり、肉厚中央部に存在する延伸したMnSの長さが150μm以下であり、ロックウェルBスケールの硬さ(HRB)が95以下、肉厚/外径比が0.14以上であり、内表面部の脱炭層深さが、内表面から20μm以下であることを特徴とする中空スタビライザ用鋼管。
logVc90=2.94-0.75β ・・・ (式1)
ただし、β=2.7C+0.4Si+Mn+0.8Cr+2.0Mo+0.8Niである。 - 請求項5に記載の中空スタビライザ用鋼管を製造する方法において、該鋼管が電縫鋼管であって、電縫溶接後に800~1200℃に加熱し、断面減少率が40~80%の範囲になるように熱間で縮径圧延する工程を含むことを特徴とする中空スタビライザ用鋼管の製造方法。
- 請求項5に記載の中空スタビライザ用鋼管を製造する方法において、該鋼管が電縫鋼管であって、電縫溶接後に冷間で引抜加工して伸管する工程を含むことを特徴とする中空スタビライザ用鋼管の製造方法。
Priority Applications (9)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
BR112014028915-8A BR112014028915B1 (pt) | 2012-05-25 | 2013-02-25 | Estabilizador oco, e tubo de aço para estabilizadores ocos e método de produção dos mesmos |
CN201380026477.0A CN104395487B (zh) | 2012-05-25 | 2013-02-25 | 空心稳定杆和空心稳定杆用钢管及其制造方法 |
IN10254DEN2014 IN2014DN10254A (ja) | 2012-05-25 | 2013-02-25 | |
MX2014014205A MX358844B (es) | 2012-05-25 | 2013-02-25 | Estabilizador hueco y tuberia de acero para estabilizadores huecos y metodo de produccion de los mismos. |
US14/402,745 US20150176101A1 (en) | 2012-05-25 | 2013-02-25 | Hollow stabilizer, and steel pipe for hollow stabilizers and method of producing the same |
JP2013527395A JP6225026B2 (ja) | 2012-05-25 | 2013-02-25 | 中空スタビライザ並びに中空スタビライザ用鋼管及びその製造方法 |
KR1020147034120A KR101706839B1 (ko) | 2012-05-25 | 2013-02-25 | 중공 스태빌라이저 및 중공 스태빌라이저용 강관 및 그 제조 방법 |
ES13794071.4T ES2691085T3 (es) | 2012-05-25 | 2013-02-25 | Estabilizador hueco, y tubo de acero para estabilizadores huecos y método para producir el mismo |
EP13794071.4A EP2857537B1 (en) | 2012-05-25 | 2013-02-25 | Hollow stabilizer, and steel pipe for hollow stabilizers and method for production thereof |
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP2012119869 | 2012-05-25 | ||
JP2012-119869 | 2012-05-25 |
Publications (1)
Publication Number | Publication Date |
---|---|
WO2013175821A1 true WO2013175821A1 (ja) | 2013-11-28 |
Family
ID=49623526
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
PCT/JP2013/054815 WO2013175821A1 (ja) | 2012-05-25 | 2013-02-25 | 中空スタビライザ並びに中空スタビライザ用鋼管及びその製造方法 |
Country Status (11)
Country | Link |
---|---|
US (1) | US20150176101A1 (ja) |
EP (1) | EP2857537B1 (ja) |
JP (1) | JP6225026B2 (ja) |
KR (1) | KR101706839B1 (ja) |
CN (1) | CN104395487B (ja) |
BR (1) | BR112014028915B1 (ja) |
ES (1) | ES2691085T3 (ja) |
HU (1) | HUE040155T2 (ja) |
IN (1) | IN2014DN10254A (ja) |
MX (1) | MX358844B (ja) |
WO (1) | WO2013175821A1 (ja) |
Cited By (15)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN104451334A (zh) * | 2014-11-17 | 2015-03-25 | 柳州市俊杰汽配制造有限公司 | 一种汽车用刹车碟 |
CN104451332A (zh) * | 2014-11-17 | 2015-03-25 | 柳州市俊杰汽配制造有限公司 | 一种汽车用悬架 |
CN104451330A (zh) * | 2014-11-17 | 2015-03-25 | 柳州市俊杰汽配制造有限公司 | 一种汽车用平衡杆 |
JP2015168845A (ja) * | 2014-03-06 | 2015-09-28 | 新日鐵住金株式会社 | 疲労特性に優れた中空材とその製造方法 |
JP2016179765A (ja) * | 2015-03-24 | 2016-10-13 | 日本発條株式会社 | 中空スタビライザ |
EP3124638A4 (en) * | 2014-03-24 | 2017-03-01 | JFE Bars & Shapes Corporation | Stabilizer steel having high strength and excellent corrosion resistance, vehicle stabilizer employing same, and method for manufacturing same |
WO2017056384A1 (ja) * | 2015-09-29 | 2017-04-06 | Jfeスチール株式会社 | 高強度中空スタビライザー用電縫鋼管、高強度中空スタビライザー用電縫鋼管の製造方法、高強度中空スタビライザー、および高強度中空スタビライザーの製造方法 |
WO2017170790A1 (ja) * | 2016-03-30 | 2017-10-05 | 日本発條株式会社 | 中空ばね部材 |
KR101799714B1 (ko) | 2014-02-04 | 2017-11-20 | 신닛테츠스미킨 카부시키카이샤 | 강관 |
WO2018079398A1 (ja) * | 2016-10-24 | 2018-05-03 | Jfeスチール株式会社 | 高強度薄肉中空スタビライザー用電縫鋼管およびその製造方法 |
EP3281814A4 (en) * | 2015-03-24 | 2018-11-21 | NHK Spring Co., Ltd. | Method for producing hollow stabilizer |
WO2019003477A1 (ja) * | 2017-06-28 | 2019-01-03 | 三菱製鋼株式会社 | 中空スタビライザー及びその製造方法 |
WO2019188224A1 (ja) * | 2018-03-29 | 2019-10-03 | Jfeスチール株式会社 | 中空スタビライザー製造用の電縫鋼管、中空スタビライザー、及びそれらの製造方法 |
WO2020230795A1 (ja) * | 2019-05-13 | 2020-11-19 | Jfeスチール株式会社 | 中空スタビライザー用電縫鋼管 |
US11254177B2 (en) | 2016-03-30 | 2022-02-22 | Nhk Spring Co., Ltd. | Hollow coil spring and suspension device for vehicle |
Families Citing this family (15)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP2015209015A (ja) * | 2014-04-24 | 2015-11-24 | 日本発條株式会社 | 中空スタビライザ |
DE102015217401B4 (de) * | 2015-09-11 | 2018-04-05 | Thyssenkrupp Ag | Rohrfeder für Kraftfahrzeuge und ein Verfahren zum Herstellen einer Rohrfeder |
JP6535617B2 (ja) * | 2016-02-09 | 2019-06-26 | 日本発條株式会社 | 車両用スタビライザと、スタビライザのためのショットピーニング用治具 |
KR101879108B1 (ko) * | 2016-12-23 | 2018-07-16 | 주식회사 포스코 | 스태빌라이저 바의 제조방법 |
CN109722503A (zh) * | 2017-10-27 | 2019-05-07 | 上海中国弹簧制造有限公司 | 空心稳定杆端头的加工工艺 |
MX2020013761A (es) * | 2018-06-27 | 2021-03-02 | Jfe Steel Corp | Tubo de acero soldado por resistencia electrica para la produccion de estabilizador hueco, estabilizador hueco, y metodo para la produccion de los mismos. |
CN109136485A (zh) * | 2018-09-30 | 2019-01-04 | 南京理工大学 | 汽车稳定杆用超高强度钢及稳定杆的制造方法 |
MX2021007336A (es) * | 2018-12-19 | 2021-07-15 | Jfe Steel Corp | Tuberia o tubo de acero soldada por resistencia electrica. |
US20220186331A1 (en) * | 2019-03-29 | 2022-06-16 | Nippon Steel Corporation | Electric resistance-welded steel tube for hollow stabilizer, hollow stabilizer, and manufacturing methods of same |
KR20200136722A (ko) * | 2019-05-28 | 2020-12-08 | 현대자동차주식회사 | 차체 멤버 성형방법 |
CN111394558B (zh) * | 2020-03-12 | 2021-12-03 | 唐山不锈钢有限责任公司 | 一种汽车空心稳定杆用钢带及其生产方法 |
MX2022011054A (es) * | 2020-03-18 | 2022-09-19 | Jfe Steel Corp | Tubo de acero soldado por resistencia electrica, metodo de fabricacion del mismo, y miembro estructural de automovil. |
CN112981255A (zh) * | 2021-02-09 | 2021-06-18 | 鞍钢股份有限公司 | 汽车空心稳定杆钢管用酸洗、eps钢板及其制造方法 |
CN115386791B (zh) * | 2022-07-13 | 2023-06-16 | 江阴兴澄特种钢铁有限公司 | 一种微合金化高强度可焊接复合稳定杆扭簧用扁钢及其制造方法 |
CN115522154B (zh) * | 2022-10-09 | 2024-04-16 | 浙江吉利控股集团有限公司 | 一种稳定杆及其制备方法、悬架总成和车辆 |
Citations (5)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP2000233625A (ja) | 1999-02-15 | 2000-08-29 | Nhk Spring Co Ltd | 中空スタビライザの製造方法 |
WO2007023873A1 (ja) | 2005-08-22 | 2007-03-01 | Nippon Steel Corporation | 焼入れ性、熱間加工性および疲労強度に優れた高強度厚肉電縫溶接鋼管およびその製造方法 |
JP2007270349A (ja) | 2006-03-09 | 2007-10-18 | Nippon Steel Corp | 中空部品用鋼管及びその製造方法 |
JP2009079280A (ja) * | 2007-09-27 | 2009-04-16 | Nisshin Steel Co Ltd | 高疲労寿命焼入れ・焼戻し鋼管およびその製造方法 |
JP2010189758A (ja) * | 2009-01-20 | 2010-09-02 | Nippon Steel Corp | 疲労強度に優れる鋼管の製造方法 |
Family Cites Families (10)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS57126917A (en) * | 1981-01-30 | 1982-08-06 | Nisshin Steel Co Ltd | Production of hollow stabilizer |
JP4443910B2 (ja) * | 2003-12-12 | 2010-03-31 | Jfeスチール株式会社 | 自動車構造部材用鋼材およびその製造方法 |
JP4510515B2 (ja) * | 2004-05-21 | 2010-07-28 | 新日本製鐵株式会社 | 疲労特性に優れた中空部品 |
JP4506486B2 (ja) * | 2005-01-31 | 2010-07-21 | Jfeスチール株式会社 | 高強度中空スタビライザ用電縫鋼管および高強度中空スタビライザの製造方法 |
JP2007023873A (ja) | 2005-07-15 | 2007-02-01 | Nikki Co Ltd | ロータリースロットル弁式気化器における燃料供給管の固定手段 |
CN101248202A (zh) * | 2005-08-22 | 2008-08-20 | 新日本制铁株式会社 | 淬透性、热加工性及疲劳强度优异的高强度厚壁电焊钢管及其制造方法 |
JP5303842B2 (ja) * | 2007-02-26 | 2013-10-02 | Jfeスチール株式会社 | 偏平性に優れた熱処理用電縫溶接鋼管の製造方法 |
JP5353256B2 (ja) * | 2008-01-21 | 2013-11-27 | Jfeスチール株式会社 | 中空部材およびその製造方法 |
JP2009235499A (ja) * | 2008-03-27 | 2009-10-15 | Nisshin Steel Co Ltd | 中空スタビライザーの製造方法 |
JP5287164B2 (ja) * | 2008-11-18 | 2013-09-11 | Jfeスチール株式会社 | 耐腐食疲労特性に優れた高強度中空部材用電縫溶接鋼管 |
-
2013
- 2013-02-25 CN CN201380026477.0A patent/CN104395487B/zh active Active
- 2013-02-25 EP EP13794071.4A patent/EP2857537B1/en active Active
- 2013-02-25 ES ES13794071.4T patent/ES2691085T3/es active Active
- 2013-02-25 WO PCT/JP2013/054815 patent/WO2013175821A1/ja active Application Filing
- 2013-02-25 BR BR112014028915-8A patent/BR112014028915B1/pt active IP Right Grant
- 2013-02-25 US US14/402,745 patent/US20150176101A1/en not_active Abandoned
- 2013-02-25 KR KR1020147034120A patent/KR101706839B1/ko active IP Right Grant
- 2013-02-25 MX MX2014014205A patent/MX358844B/es active IP Right Grant
- 2013-02-25 HU HUE13794071A patent/HUE040155T2/hu unknown
- 2013-02-25 IN IN10254DEN2014 patent/IN2014DN10254A/en unknown
- 2013-02-25 JP JP2013527395A patent/JP6225026B2/ja active Active
Patent Citations (5)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP2000233625A (ja) | 1999-02-15 | 2000-08-29 | Nhk Spring Co Ltd | 中空スタビライザの製造方法 |
WO2007023873A1 (ja) | 2005-08-22 | 2007-03-01 | Nippon Steel Corporation | 焼入れ性、熱間加工性および疲労強度に優れた高強度厚肉電縫溶接鋼管およびその製造方法 |
JP2007270349A (ja) | 2006-03-09 | 2007-10-18 | Nippon Steel Corp | 中空部品用鋼管及びその製造方法 |
JP2009079280A (ja) * | 2007-09-27 | 2009-04-16 | Nisshin Steel Co Ltd | 高疲労寿命焼入れ・焼戻し鋼管およびその製造方法 |
JP2010189758A (ja) * | 2009-01-20 | 2010-09-02 | Nippon Steel Corp | 疲労強度に優れる鋼管の製造方法 |
Cited By (34)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
KR101799714B1 (ko) | 2014-02-04 | 2017-11-20 | 신닛테츠스미킨 카부시키카이샤 | 강관 |
JP2015168845A (ja) * | 2014-03-06 | 2015-09-28 | 新日鐵住金株式会社 | 疲労特性に優れた中空材とその製造方法 |
EP3124638A4 (en) * | 2014-03-24 | 2017-03-01 | JFE Bars & Shapes Corporation | Stabilizer steel having high strength and excellent corrosion resistance, vehicle stabilizer employing same, and method for manufacturing same |
CN104451330A (zh) * | 2014-11-17 | 2015-03-25 | 柳州市俊杰汽配制造有限公司 | 一种汽车用平衡杆 |
CN104451332A (zh) * | 2014-11-17 | 2015-03-25 | 柳州市俊杰汽配制造有限公司 | 一种汽车用悬架 |
CN104451334A (zh) * | 2014-11-17 | 2015-03-25 | 柳州市俊杰汽配制造有限公司 | 一种汽车用刹车碟 |
EP3281814A4 (en) * | 2015-03-24 | 2018-11-21 | NHK Spring Co., Ltd. | Method for producing hollow stabilizer |
JP2016179765A (ja) * | 2015-03-24 | 2016-10-13 | 日本発條株式会社 | 中空スタビライザ |
US10442269B2 (en) | 2015-03-24 | 2019-10-15 | Nhk Spring Co., Ltd. | Hollow stabilizer |
US10415110B2 (en) | 2015-03-24 | 2019-09-17 | Nhk Spring Co., Ltd. | Method for producing hollow stabilizer |
WO2017056384A1 (ja) * | 2015-09-29 | 2017-04-06 | Jfeスチール株式会社 | 高強度中空スタビライザー用電縫鋼管、高強度中空スタビライザー用電縫鋼管の製造方法、高強度中空スタビライザー、および高強度中空スタビライザーの製造方法 |
JPWO2017056384A1 (ja) * | 2015-09-29 | 2017-10-05 | Jfeスチール株式会社 | 高強度中空スタビライザー用電縫鋼管、高強度中空スタビライザー用電縫鋼管の製造方法、高強度中空スタビライザー、および高強度中空スタビライザーの製造方法 |
US10787720B2 (en) | 2015-09-29 | 2020-09-29 | Jfe Steel Corporation | Electric resistance welded steel pipe for high-strength hollow stabilizer, and method for manufacturing electric resistance welded steel pipe for high-strength hollow stabilizer |
CN109154346A (zh) * | 2016-03-30 | 2019-01-04 | 日本发条株式会社 | 中空弹簧构件 |
US11254177B2 (en) | 2016-03-30 | 2022-02-22 | Nhk Spring Co., Ltd. | Hollow coil spring and suspension device for vehicle |
US11701943B2 (en) | 2016-03-30 | 2023-07-18 | Nhk Spring Co., Ltd | Method of manufacturing a hollow spring member |
JPWO2017170790A1 (ja) * | 2016-03-30 | 2018-10-25 | 日本発條株式会社 | 中空ばね部材 |
US11685211B2 (en) | 2016-03-30 | 2023-06-27 | Nhk Spring Co., Ltd | Hollow coil spring and suspension device for vehicle |
WO2017170790A1 (ja) * | 2016-03-30 | 2017-10-05 | 日本発條株式会社 | 中空ばね部材 |
JPWO2018079398A1 (ja) * | 2016-10-24 | 2018-11-01 | Jfeスチール株式会社 | 高強度薄肉中空スタビライザー用電縫鋼管およびその製造方法 |
WO2018079398A1 (ja) * | 2016-10-24 | 2018-05-03 | Jfeスチール株式会社 | 高強度薄肉中空スタビライザー用電縫鋼管およびその製造方法 |
US11332812B2 (en) | 2016-10-24 | 2022-05-17 | Jfe Steel Corporation | Electric resistance welded steel tubes for high-strength thin hollow stabilizers, and methods for manufacturing the same |
US10987779B2 (en) | 2017-06-28 | 2021-04-27 | Mitsubishi Steel Mfg. Co., Ltd. | Hollow spring and manufacturing method thereof |
RU2741437C1 (ru) * | 2017-06-28 | 2021-01-26 | Мицубиси Стил Мфг. Ко., Лтд. | Полая пружина и способ ее изготовления |
WO2019003477A1 (ja) * | 2017-06-28 | 2019-01-03 | 三菱製鋼株式会社 | 中空スタビライザー及びその製造方法 |
JPWO2019004375A1 (ja) * | 2017-06-28 | 2019-11-07 | 三菱製鋼株式会社 | 中空ばね及びその製造方法 |
WO2019004375A1 (ja) * | 2017-06-28 | 2019-01-03 | 三菱製鋼株式会社 | 中空ばね及びその製造方法 |
US11440125B2 (en) | 2018-03-29 | 2022-09-13 | Jfe Steel Corporation | Electric resistance welded steel pipe for producing hollow stabilizer, hollow stabilizer, and production methods for same |
WO2019188224A1 (ja) * | 2018-03-29 | 2019-10-03 | Jfeスチール株式会社 | 中空スタビライザー製造用の電縫鋼管、中空スタビライザー、及びそれらの製造方法 |
JPWO2020230795A1 (ja) * | 2019-05-13 | 2021-05-20 | Jfeスチール株式会社 | 中空スタビライザー用電縫鋼管 |
CN113811625A (zh) * | 2019-05-13 | 2021-12-17 | 杰富意钢铁株式会社 | 中空稳定器用电阻焊钢管 |
WO2020230795A1 (ja) * | 2019-05-13 | 2020-11-19 | Jfeスチール株式会社 | 中空スタビライザー用電縫鋼管 |
JP7070696B2 (ja) | 2019-05-13 | 2022-05-18 | Jfeスチール株式会社 | 中空スタビライザー用電縫鋼管 |
CN113811625B (zh) * | 2019-05-13 | 2023-12-15 | 杰富意钢铁株式会社 | 中空稳定器用电阻焊钢管 |
Also Published As
Publication number | Publication date |
---|---|
BR112014028915A2 (pt) | 2017-06-27 |
KR101706839B1 (ko) | 2017-02-14 |
JPWO2013175821A1 (ja) | 2016-01-12 |
HUE040155T2 (hu) | 2019-02-28 |
CN104395487A (zh) | 2015-03-04 |
EP2857537A1 (en) | 2015-04-08 |
MX358844B (es) | 2018-09-05 |
JP6225026B2 (ja) | 2017-11-01 |
BR112014028915B1 (pt) | 2019-05-14 |
EP2857537A4 (en) | 2016-04-13 |
US20150176101A1 (en) | 2015-06-25 |
MX2014014205A (es) | 2015-02-12 |
ES2691085T3 (es) | 2018-11-23 |
IN2014DN10254A (ja) | 2015-08-07 |
CN104395487B (zh) | 2017-02-22 |
KR20150013247A (ko) | 2015-02-04 |
EP2857537B1 (en) | 2018-07-25 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
JP6225026B2 (ja) | 中空スタビライザ並びに中空スタビライザ用鋼管及びその製造方法 | |
JP5353256B2 (ja) | 中空部材およびその製造方法 | |
EP3239339B1 (en) | Product formed from heat treatable steel having ultra high strength and excellent durability, and method for manufacturing same | |
KR101668546B1 (ko) | 내변형 시효 특성이 우수한 저항복비 고강도 강판 및 그 제조 방법 그리고 그것을 사용한 고강도 용접 강관 | |
US8007601B2 (en) | Methods of producing high-strength metal tubular bars possessing improved cold formability | |
US11332812B2 (en) | Electric resistance welded steel tubes for high-strength thin hollow stabilizers, and methods for manufacturing the same | |
JP5005543B2 (ja) | 焼入れ性、熱間加工性および疲労強度に優れた高強度厚肉電縫溶接鋼管およびその製造方法 | |
JP5391656B2 (ja) | 自動車部材用高張力溶接鋼管およびその製造方法 | |
JP4910694B2 (ja) | 自動車構造部材用高張力溶接鋼管及びその製造方法 | |
JP2009242858A (ja) | 高強度鋼管およびその製造方法 | |
JP2009191330A (ja) | 電縫鋼管 | |
JP5125601B2 (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 | |
JP5206755B2 (ja) | 高強度ラインパイプ用鋼板の製造方法 | |
JPWO2020003720A1 (ja) | 中空スタビライザー製造用の電縫鋼管、中空スタビライザー、及びそれらの製造方法 | |
JPS58123858A (ja) | 中空状スタビライザ−用電縫鋼管用鋼 | |
CN113631735B (zh) | 中空稳定器用电焊钢管和中空稳定器、以及其制造方法 | |
JP5516780B2 (ja) | 偏平性に優れた熱処理用電縫溶接鋼管 | |
JP5842577B2 (ja) | 耐歪時効性に優れた高靱性低降伏比高強度鋼板 | |
JP2023534826A (ja) | トーションビーム用鋼板およびその製造方法、トーションビームおよびその製造方法 | |
JP5942572B2 (ja) | 耐疲労特性に優れた自動車部品用電縫溶接鋼管およびその製造方法 | |
JP5512231B2 (ja) | 静的ねじり強度に優れたドライブシャフト用電縫鋼管およびその製造方法 |
Legal Events
Date | Code | Title | Description |
---|---|---|---|
ENP | Entry into the national phase |
Ref document number: 2013527395 Country of ref document: JP Kind code of ref document: A |
|
121 | Ep: the epo has been informed by wipo that ep was designated in this application |
Ref document number: 13794071 Country of ref document: EP Kind code of ref document: A1 |
|
WWE | Wipo information: entry into national phase |
Ref document number: 14402745 Country of ref document: US Ref document number: MX/A/2014/014205 Country of ref document: MX |
|
NENP | Non-entry into the national phase |
Ref country code: DE |
|
ENP | Entry into the national phase |
Ref document number: 20147034120 Country of ref document: KR Kind code of ref document: A |
|
REG | Reference to national code |
Ref country code: BR Ref legal event code: B01A Ref document number: 112014028915 Country of ref document: BR |
|
WWE | Wipo information: entry into national phase |
Ref document number: 2013794071 Country of ref document: EP |
|
ENP | Entry into the national phase |
Ref document number: 112014028915 Country of ref document: BR Kind code of ref document: A2 Effective date: 20141119 |