WO2011108675A1 - 高強度中空ばね用シームレス鋼管 - Google Patents
高強度中空ばね用シームレス鋼管 Download PDFInfo
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- WO2011108675A1 WO2011108675A1 PCT/JP2011/054986 JP2011054986W WO2011108675A1 WO 2011108675 A1 WO2011108675 A1 WO 2011108675A1 JP 2011054986 W JP2011054986 W JP 2011054986W WO 2011108675 A1 WO2011108675 A1 WO 2011108675A1
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- 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
- B21C23/00—Extruding metal; Impact extrusion
- B21C23/002—Extruding materials of special alloys so far as the composition of the alloy requires or permits special extruding methods of sequences
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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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/18—Hardening; Quenching with or without subsequent tempering
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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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/26—Methods of annealing
- C21D1/32—Soft annealing, e.g. spheroidising
-
- 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
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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
- C21D9/02—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for springs
-
- 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
- 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
- C22C38/34—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of silicon
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
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- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F16—ENGINEERING ELEMENTS AND UNITS; GENERAL MEASURES FOR PRODUCING AND MAINTAINING EFFECTIVE FUNCTIONING OF MACHINES OR INSTALLATIONS; THERMAL INSULATION IN GENERAL
- F16L—PIPES; JOINTS OR FITTINGS FOR PIPES; SUPPORTS FOR PIPES, CABLES OR PROTECTIVE TUBING; MEANS FOR THERMAL INSULATION IN GENERAL
- F16L9/00—Rigid pipes
- F16L9/02—Rigid pipes of metal
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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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/001—Austenite
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/003—Cementite
Definitions
- the present invention relates to a high-strength seamless steel pipe for a hollow spring, and particularly to a high-quality seamless steel pipe suitable for manufacturing a hollow suspension spring used in an automobile.
- a coil spring is formed by winding a solid wire.
- a hollow wire that is, a tubular one has already been proposed in Patent Document 1 and the like. Although it has been known for a long time, it was difficult to manufacture and the past market needs were not so strong.
- this hollow suspension spring is formed from a small diameter steel pipe having a diameter of about 16 mm (sometimes simply referred to as a pipe) with hot or cold spring formation, followed by heat treatment such as quenching and tempering. Setting and shot peening are performed to make a product, but since the steel pipe used as the material greatly affects the characteristics of the suspension spring, it is important to maintain and improve the quality of the material steel pipe.
- an electric resistance welded pipe (welded pipe) was originally considered from the viewpoint of manufacturing cost, but the spring steel (JISG4801) is generally a high C steel containing 0.5% or more of C, and Since it contains alloy elements such as Si and Mn, it has been found that it is not suitable for production that requires pipe making and welding processes, and application of seamless steel pipes has been studied.
- Patent Documents 3 and 4 propose a technique using the latter hot extrusion method. Both techniques disclosed in both documents employ isostatic pressing as a hot extrusion method.
- This invention is made
- the present invention proposes a seamless steel pipe for a high-strength hollow spring having the following contents as a means for solving the above-mentioned problems.
- C 0.20 to 0.70 mass%, Si: 0.5 to 3.0 mass%, Mn: 0.1 to 3.0 mass%, P: 0.030 mass% or less (0% S: 0.030% by mass or less (including 0%), N: 0.02% by mass or less (including 0%), the balance Fe and unavoidable impurities, and the carbide has an equivalent circle diameter of 1
- a seamless steel pipe for a high-strength hollow spring characterized by being 0.000 ⁇ m or less.
- suspension parts such as suspension springs
- further weight reduction of vehicles such as automobiles
- Metal structure of the steel pipe (1)
- the carbide size is equivalent to a circle and is 1.00 ⁇ m or less
- carbide of metal elements such as cementite (Fe 3 C) existing in the metal structure of the seamless steel pipe (M 3 C, M 7 C 3 , M 23 C 6, etc.) are equivalent to a circle and are 1.00 ⁇ m or less in size.
- the carbide of the metal element referred to here includes the cementite, carbides such as Mn, Cr, V, Ti, Nb, Ta, and Hf, and composite carbides thereof, and further, a part of the carbides and composite carbides. It means a carbide containing Fe.
- the size of this carbide may be 1.00 ⁇ m or less. However, the finer the material, the easier it is to form a solid solution at the time of heating in the quenching process. It is advantageous for improving durability. Accordingly, the size of the carbide is preferably 0.80 ⁇ m or less, more preferably 0.60 ⁇ m or less, and still more preferably 0.40 ⁇ m or less.
- the heating temperature in the final annealing step In other words, the annealing temperature may be higher than 750 ° C.
- spheroidizing annealing for spheroidizing carbides in steel is performed a plurality of times in order to improve workability.
- conventional spheroidization is performed in the final annealing step of this annealing.
- high-temperature annealing is adopted in which carbides are dissolved at an annealing temperature exceeding 750 ° C.
- the heating temperature may be set to a high temperature exceeding 750 ° C. not only in the final annealing step but also in some or all of the remaining annealing steps.
- the heat treatment temperature is set to 650 to 750 ° C., and even if it exceeds 750 ° C., the annealing effect is saturated and it is economically undesirable.
- the carbide does not dissolve during annealing and remains coarse. Therefore, in the present invention, carbide is completely dissolved during annealing by adopting high-temperature annealing different from the conventional technique that heats to 750 ° C. or less, and coarse carbide is eliminated. Needless to say, the high-temperature annealing can soften the steel material and simultaneously improve the workability.
- the solid-dissolved carbide is reprecipitated, but the reprecipitated carbide has a fine size of 1.00 ⁇ m or less, and thus the seamless steel pipe having the metal structure of the present invention is obtained.
- the final annealing temperature is higher than 750 ° C., the carbide is completely dissolved, and the seamless steel pipe targeted by the present invention can be obtained.
- the annealing time is short because of deterioration.
- An increase in the heating temperature is effective for shortening the annealing time. If the heating temperature is high, the solid solution of the carbide is completed in a short time.
- the final annealing temperature is preferably 800 ° C. or higher, more preferably 850 ° C. or higher, still more preferably 900 ° C. or higher, and still more preferably 925 ° C. or higher.
- the annealing temperature is preferably 1000 ° C. or less.
- the cooling in the final annealing is preferably air cooling, and the cooling rate is preferably 0.5 to 10 ° C./sec.
- Patent Document 3 proposes the hot isostatic pressing method, or a rolling method or the like. Any processing method can be adopted for the processing conditions.
- a block-rolled billet adjusted to the component range of the high-strength spring steel defined in the present invention has an outer diameter of 143 mm and a wall thickness of, for example. Molded into a 52 mm steel pipe billet.
- the formed cylindrical billet is heated to 1050 to 1300 ° C., it is hot processed by a hot extrusion device to obtain a steel pipe first intermediate.
- the first intermediate is heated to 650 to 750 ° C. to perform first intermediate annealing.
- the first intermediate that has undergone the intermediate annealing is subjected to a first cold working by a Pilger mill rolling machine or a drawing machine to obtain a steel pipe second intermediate.
- the second intermediate annealing is performed by heating the steel pipe second intermediate to 650 to 750 ° C. as in the case of the first intermediate.
- the second intermediate body subjected to the second intermediate annealing is subjected to a second cold working by a Pilger mill rolling machine or a drawing machine to obtain a steel pipe third intermediate body.
- the steel pipe third intermediate is heated to a high temperature of more than 750 ° C. to 1000 ° C. to perform final annealing.
- the steel pipe thus obtained is subjected to purification such as straightening and pickling to finally obtain a product (seamless steel pipe) having an outer diameter of 16 mm and a wall thickness of 4 mm, for example.
- the intermediate annealing after the hot working can be omitted, and also necessary in the intermediate annealing process other than the final annealing as described for the application of the high temperature annealing of the present invention in each of the previous annealing processes. Accordingly, high temperature annealing exceeding 750 ° C. may be adopted.
- C 0.20 to 0.70% C has a great influence on the strength of steel. In order to apply to a high-strength spring, addition of 0.20% or more is necessary. On the other hand, when C is increased, brittle lens martensite is generated at the time of quenching, and the spring fatigue characteristics are deteriorated. Therefore, it is necessary to make it 0.70% or less.
- the lower limit of the C amount is more preferably 0.30% or more, further preferably 035% or more, and further preferably 0.40% or more, and the upper limit is more preferably 0.65% or less. More preferably, it is 0.60% or less, more preferably 0.55% or less.
- Si 0.5 to 3.0% It is known that Si has a large temper softening resistance at 500 ° C. or less. It is an element necessary for securing the strength of a spring that performs tempering treatment at a relatively low temperature, and 0.5% or more must be added. On the other hand, the Si increase suppresses cementite precipitation during tempering and increases the residual ⁇ . However, the spring characteristics deteriorate due to the increase in the residual ⁇ , so it is necessary to make it 3.0% or less. Further, the lower limit of the Si amount is more preferably 1.0% or more, still more preferably 1.4% or more, still more preferably 1.7% or more, and the upper limit thereof is more preferably 2.8. % Or less, more preferably 2.6% or less, and still more preferably 2.4% or less.
- Mn 0.1 to 3.0% Mn fixes the harmful element S as MnS and suppresses toughness deterioration. For that purpose, addition of 0.1% or more is necessary. On the other hand, Mn is dissolved and stabilized in cementite. However, if the Mn ratio in the cementite is increased by increasing the amount of Mn, the cementite is difficult to dissolve during heating. Therefore, it is necessary to set it as 3.0% or less.
- the lower limit of the amount of Mn is more preferably 0.15% or more, still more preferably 0.20% or more, still more preferably 0.30% or more, and the upper limit is more preferably 2.5%. Hereinafter, it is more preferably 2.0% or less, and still more preferably 1.5% or less.
- P 0.030% or less (including 0%) P is preferably as low as possible because it segregates at grain boundaries and degrades toughness. In order to ensure the characteristics as a high-strength spring, it is necessary to make it 0.030% or less.
- the upper limit of the amount of P is more preferably 0.020% or less, still more preferably 0.015% or less, and still more preferably 0.010% or less.
- S: 0.030% or less (including 0%) S is preferably as low as possible because it causes toughness degradation due to grain boundary embrittlement and coarse sulfide formation. In order to ensure the characteristics as a high-strength spring, it is necessary to control to 0.030% or less.
- the upper limit of the amount of S is more preferably 0.020% or less, still more preferably 0.015% or less, and still more preferably 0.010% or less.
- N 0.02% or less (including 0%) N forms nitrides with Al, Ti, etc., and contributes to the improvement of toughness by refining the structure, but when it exists in a solid solution state, it deteriorates toughness. Therefore, in this invention, it is necessary to make N amount 0.02% or less.
- this N amount is more preferably 0.015% or less, still more preferably 0.010% or less, and still more preferably 0.005% or less.
- Cr 3.0% or less (excluding 0%) Cr is effective for securing the strength after tempering and improving the corrosion resistance, and is an element advantageous for increasing the strength of the spring. In order to exert this effect, addition of 0.20% or more is preferable.
- Cr is solid-solved in cementite and stabilized. However, if the Cr ratio in the cementite is increased by increasing the amount of Cr, it is difficult to dissolve the cementite during heating.
- the lower limit of the Cr amount is more preferably 0.40% or more, further preferably 0.60% or more, still more preferably 0.80% or more, and the upper limit thereof is more preferably 2.5. % Or less, more preferably 2.0% or less, and still more preferably 1.5% or less.
- (8) B: 0.0150% or less (excluding 0%) B has the effect of reducing the grain boundary segregation of P and suppressing toughness deterioration. In order to exhibit this effect, 0.0010% or more may be added. On the other hand, if added excessively, coarse boric boride is generated, which causes a decrease in strength and a deterioration in toughness.
- the lower limit of the B amount is more preferably 0.0015% or more, further preferably 0.0020% or more, and further preferably 0.0025% or more.
- the upper limit is more preferably 0.0120. % Or less, more preferably 0.0100% or less, and still more preferably 0.0070% or less.
- Al like Si, has the effect of suppressing cementite precipitation during tempering and increasing the residual ⁇ , and when the amount of Al is increased, the spring characteristics deteriorate due to the increase in residual ⁇ . For this reason, it is necessary to set it as 0.10% or less.
- the lower limit of the Al amount is more preferably 0.002% or more, still more preferably 0.005% or more, still more preferably 0.010% or more, and the upper limit is more preferably 0.070%. % Or less, more preferably 0.050% or less, and still more preferably 0.030% or less.
- V 1.0% or less (excluding 0%) V forms carbonitrides, contributes to the refinement of the structure, and is effective in improving toughness. In order to exert this effect, 0.020% or more may be added. However, excessive addition makes the carbonitride coarse and deteriorates toughness. From this viewpoint, it is necessary to be 1.0% or less. Furthermore, the minimum addition is desirable from the viewpoint of cost reduction.
- the lower limit of the V amount is more preferably 0.030% or more, still more preferably 0.050% or more, still more preferably 0.070% or more, and the upper limit is more preferably 0.50. % Or less, more preferably 0.30% or less, and still more preferably 0.20% or less.
- Ti 0.30% or less (excluding 0%) Ti forms carbonitrides and contributes to the refinement of the structure, and is effective in improving toughness. In order to exert this effect, 0.020% or more may be added. However, excessive addition makes the carbonitride coarse and deteriorates toughness. From this viewpoint, it is necessary to be 0.30% or less. Furthermore, the minimum addition is desirable from the viewpoint of cost reduction.
- the lower limit of the Ti amount is more preferably 0.030% or more, still more preferably 0.050% or more, still more preferably 0.070% or more, and the upper limit is more preferably 0.25. % Or less, more preferably 0.20% or less, and still more preferably 0.15% or less.
- Nb 0.30% or less (excluding 0%) Nb forms carbonitrides and contributes to refinement of the structure, and is effective in improving toughness. In order to exert this effect, 0.02% or more may be added. However, excessive addition makes the carbonitride coarse and deteriorates toughness. From this viewpoint, it is necessary to be 0.30% or less. Furthermore, the minimum addition is desirable from the viewpoint of cost reduction.
- the lower limit of the Nb amount is more preferably 0.030% or more, further preferably 0.050% or more, still more preferably 0.070% or more, and the upper limit is more preferably 0.25. % Or less, more preferably 0.20% or less, and still more preferably 0.15% or less.
- Ni 3.0% or less (excluding 0%) Ni is known to improve toughness by addition, and also has an effect of suppressing decarburization during heating, contributing to improvement of spring durability characteristics. In order to exert these effects, 0.1% or more may be added. On the other hand, excessive addition increases the residual ⁇ and degrades the spring characteristics. Therefore, it is necessary to make it 3.0% or less. Furthermore, the minimum addition is desirable from the viewpoint of cost reduction.
- the lower limit of the Ni amount is more preferably 0.20% or more, further preferably 0.40% or more, and further preferably 0.60% or more.
- the upper limit thereof is more preferably 2.5. % Or less, more preferably 2.0% or less, and still more preferably 1.5% or less.
- Cu: 3.0% or less (excluding 0%) Cu has an effect of suppressing decarburization during heating, and contributes to improvement of spring durability characteristics. In order to exhibit this effect, 0.10% or more may be added. On the other hand, excessive addition increases the residual ⁇ and degrades the spring characteristics. Therefore, it is necessary to make it 3.0% or less. Furthermore, the minimum addition is desirable from the viewpoint of cost reduction.
- the lower limit of the Cu amount is more preferably 0.20% or more, still more preferably 0.40% or more, still more preferably 0.60% or more, and the upper limit thereof is more preferably 2.5. % Or less, more preferably 2.0% or less, and still more preferably 1.5% or less.
- Mo 2.0% or less (excluding 0%) Mo has the effect of reducing the grain boundary segregation of P and suppressing toughness deterioration. Moreover, it forms carbides and contributes to the refinement of the structure, improving the toughness. In order to exhibit these effects, addition of 0.2% or more is necessary. On the other hand, when excessively added, a remarkable solidification segregation zone is formed, resulting in toughness deterioration. Therefore, it is necessary to make it 2.0% or less. Furthermore, the minimum addition is desirable from the viewpoint of cost reduction.
- the lower limit of the Mo amount is more preferably 0.30% or more, still more preferably 0.50% or more, still more preferably 0.70% or more, and the upper limit is more preferably 1.8. % Or less, more preferably 1.6% or less, and still more preferably 1.4% or less.
- Ca 0.0050% or less (excluding 0%) Ca contributes to the improvement of toughness by making the sulfide finer by adding a small amount. In order to exhibit this effect, 0.0001% or more may be added. On the other hand, excessive addition causes toughness degradation. Therefore, it is necessary to make it 0.0050% or less.
- the lower limit of the Ca content is more preferably 0.0002% or more, still more preferably 0.0003% or more, still more preferably 0.0004% or more, and the upper limit thereof is more preferably 0.0030%. % Or less, more preferably 0.0020% or less, and still more preferably 0.0010% or less.
- Mg 0.0050% or less (excluding 0%) Mg contributes to improving toughness by adding a small amount of sulfide to make it finer. In order to exhibit this effect, 0.0001% or more may be added. On the other hand, excessive addition causes toughness degradation. Therefore, it is necessary to make it 0.0050% or less.
- the lower limit of this Mg amount is more preferably 0.0002% or more, still more preferably 0.0003% or more, still more preferably 0.0004% or more, and the upper limit thereof is more preferably 0.0030%. % Or less, more preferably 0.0020% or less, and still more preferably 0.0010% or less.
- REM 0.020% or less (excluding 0%) REM contributes to the improvement of toughness by adding a small amount of fine sulfide. In order to exhibit this effect, 0.0001% or more may be added. On the other hand, excessive addition causes toughness degradation. Therefore, it is necessary to make it 0.020% or less.
- the lower limit of the REM amount is more preferably 0.0002% or more, further preferably 0.0003% or more, still more preferably 0.0004% or more, and the upper limit thereof is more preferably 0.010%. % Or less, more preferably 0.0050% or less, and still more preferably 0.0010% or less.
- REM refers to a combination of lanthanoid elements (15 elements from La to Ln) and Sc and Y. (19) Zr: 0.10% or less (excluding 0%) Zr forms carbonitrides and contributes to refinement of the structure, and is effective for improving toughness. In order to exert this effect, 0.010% or more may be added. However, excessive addition makes the carbonitride coarse and deteriorates toughness. From this viewpoint, it is necessary to be 0.10% or less. Furthermore, the minimum addition is desirable from the viewpoint of cost reduction.
- the lower limit of the amount of Zr is more preferably 0.020% or more, still more preferably 0.025% or more, still more preferably 0.030% or more, and the upper limit is more preferably 0.080%. % Or less, more preferably 0.060% or less, and still more preferably 0.040% or less.
- Ta 0.10% or less (excluding 0%) Ta forms carbonitrides, contributes to the refinement of the structure, and is effective in improving toughness. In order to exert this effect, 0.01% or more may be added. However, excessive addition makes the carbonitride coarse and deteriorates toughness. From this viewpoint, it is necessary to be 0.10% or less. Furthermore, the minimum addition is desirable from the viewpoint of cost reduction.
- the lower limit of the Ta amount is more preferably 0.020% or more, further preferably 0.025% or more, and further preferably 0.030% or more.
- the upper limit is more preferably 0.080%. % Or less, more preferably 0.060% or less, and still more preferably 0.040% or less.
- the lower limit of the Hf amount is more preferably 0.020% or more, further preferably 0.025% or more, still more preferably 0.030% or more, and the upper limit is more preferably 0.080%. % Or less, more preferably 0.060% or less, and still more preferably 0.040% or less.
- the observation position was the central part of the pipe thickness (t / 2 position), and five fields of view were taken at 3000 to 5000 times.
- the observation photograph was subjected to image processing, and the carbide (cementite) in the metal structure was approximated by a circle, and the maximum value was obtained. This value is listed in Table 2 as the carbide size.
- (3) Quenching treatment of steel pipe In order to grasp the characteristics when the steel pipe is a hollow spring, the above-described seamless steel pipes were quenched (quenched and tempered). Quenching was heated to 1000 to 1150 ° C. by high frequency heating, held for 10 seconds, and then cooled with water. Moreover, tempering was air-cooled after holding at 400 ° C. for 60 minutes using an electric furnace.
- the seamless steel pipe according to the present invention has superior quality compared to the steel pipe according to the comparative example, that is, the strength after quenching treatment is 1150 MPa class or more and 100,000 times or more durability. It has been found that it has atmospheric fatigue characteristics that can withstand the test, has high strength and durability, and can be advantageously applied as a seamless steel pipe for a high-strength hollow spring.
- steel materials No. A1-1, A5-1, A6-1, A11-1, A15-1, A28-1, A29-1, A30-1, A32-1, A34-1, A35-1, A36-1 and A46-1 do not satisfy the steel component ranges defined in the present invention, respectively.
- .A7-2, A7-3, A14-2, A14-3, A18-2, A23-2, A37-2, A37-3, A42-2 and A42-3 are the carbide sizes defined in the present invention. This is because the steel materials No. A16-1 and A35-1 do not satisfy both the steel components and carbide sizes defined in the present invention.
- the seamless steel pipe of the present invention is useful for manufacturing a hollow suspension spring and the like used for automobiles.
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Abstract
Description
(1)C:0.20~0.70質量%、Si:0.5~3.0質量%、Mn:0.1~3.0質量%、P:0.030質量%以下(0%を含む)、S:0.030質量%以下(0%を含む)、N:0.02質量%以下(0%を含む)、残部Fe及び不可避的不純物からなり、炭化物が円相当径で1.00μm以下であることを特徴とする高強度中空ばね用シームレス鋼管。
(2)さらに、Cr:3.0質量%以下(0%を含まない、以下同じ)、B:0.0150質量%以下、Al:0.10質量%以下、V:1.0質量%以下、Ti:0.30質量%以下、Nb::0.30質量%以下、Ni:3.0質量%以下、Cu:3.0質量%以下、Mo:2.0質量%以下、Ca:0.0050質量%以下、Mg:0.0050質量%以下、REM:0.020質量%以下、Zr:0.10質量%以下、Ta:0.10質量%以下、Hf:0.10質量%以下から選ばれる1種以上を含有する上記(1)に記載の高強度中空ばね用シームレス鋼管。
〔1〕本鋼管の金属組織
(1)炭化物のサイズが円相当で1.00μm以下
本発明においてはシームレス鋼管の金属組織中に存在するセメンタイト(Fe3C)などの金属元素の炭化物(M3C、M7C3、M23C6など)のサイズが円相当で1.00μm以下であることが大きな特徴である。なお、ここでいう金属元素の炭化物とは、上記セメンタイトをはじめ、たとえばMn、Cr、V、Ti、Nb、Ta、Hfなどの炭化物およびこれらの複合炭化物、さらに前記炭化物や複合炭化物の一部にFeを含有する炭化物などを意味する。このように、組織中の炭化物のサイズを1.00μm以下にすることで、中空ばねの製造の際の焼入れ処理において炭化物をすばやく完全に固溶させ、且つオーステナイト粒径の粗大化も抑制され、20μm以下に小さく維持することができ、その結果、1150MPa級以上の高強度で耐久性に優れた中空ばねを製造することが可能となる。
(2)本鋼管の金属組織を得る製造方法
この本発明の金属組織における炭化物のサイズを1.00μm以下に微小化する方法としては、本発明が規定する鋼成分を有するシームレス鋼管の製造方法において、基本的には最終焼鈍工程での加熱温度すなわち焼鈍温度を750℃超にすればよい。通常、シームレス鋼管の製造にあっては加工性の改善のため鋼中の炭化物を球状化する球状化焼鈍を複数回実施するが、本発明ではこの焼鈍のうち最後の焼鈍工程において従来の球状化焼鈍に代えて、その焼鈍温度750℃超として炭化物を溶解させる高温焼鈍を採用するものである。勿論、複数の焼鈍工程が存在する場合に上記最終焼鈍工程のみならず残りの焼鈍工程の一部または全てにおいてその加熱温度を750℃超の高温として行うことも構わないものである。
本発明にかかる鋼管の成分については前記解決手段(1)及び(2)に記載の通りであり、解決手段(2)記載の元素は解決手段(1)に記載の元素にさらに選択的に添加して高強度ばねの特性を更に向上させるためのものである。これら各成分の規定理由などについて説明する。なお、%はいずれも質量%を意味する。
Cは鋼材の強度への影響が大きい。高強度ばねに適用するには0.20%以上の添加が必要である。一方で、Cを増量すると、焼入れ時に脆いレンズマルテンサイトが生成し、ばね疲労特性が劣化する。そのため0.70%以下にする必要がある。
Siは500℃以下での焼戻し軟化抵抗が大きいことが知られている。比較的低温で焼戻し処理を行うばねの強度確保に必要な元素であり0.5%以上の添加が必要である。一方で、Si増量は焼戻し時のセメンタイト析出を抑制し、残留γを増加させるが、残留γの増加によりばね特性が劣化するため3.0%以下とする必要がある。
また、このSi量の下限については、より好ましくは1.0%以上、更に好ましくは1.4%以上、一層好ましくは1.7%以上であり、その上限については、より好ましくは2.8%以下、更に好ましくは2.6%以下、一層好ましくは2.4%以下である。
Mnは有害元素SをMnSとして固定して靭性劣化を抑制する。そのためには0.1%以上の添加が必要になる。一方、Mnはセメンタイトに固溶し安定化させるが、Mn増量によってセメンタイト中のMn比が高くなると、加熱時にセメンタイトが溶解しにくくなる。よって、3.0%以下とすることが必要である。
Pは粒界偏析して靭性を劣化させるため低いほど良い。高強度ばねとしての特性を確保するためには0.030%以下とする必要がある。
(5)S:0.030%以下(0%を含む)
Sは粒界脆化や粗大硫化物形成により靭性劣化させるため低いほど良い。高強度ばねとしての特性を確保するためには0.030%以下に制御する必要がある。
(6)N:0.02%以下(0%を含む)
NはAlやTiなどと窒化物を形成し、組織微細化して靭性向上に寄与するが、固溶状態で存在すると靭性を劣化させる。そのため本発明では、N量0.02%以下とする必要がある。
(7)Cr:3.0%以下(0%を含まない)
Crは焼戻し後の強度確保や耐食性向上に有効であり、ばねの高強度化に有利な元素である。この効果を発揮させるには0.20%以上の添加が好ましい。一方、Crはセメンタイトに固溶し安定化させるが、Cr増量によってセメンタイト中のCr比が高くなると、加熱時にセメンタイトが溶解しにくくなるため3.0%以下とする必要がある。
(8)B:0.0150%以下(0%を含まない)
BはPの粒界偏析を軽減し、靭性劣化を抑制する効果がある。この効果を発現させるには0.0010%以上添加すればよい。一方、過剰添加すると粗大な炭硼化物を生成し、強度低下、靭性劣化を招くので、0.0150%以下とする必要がある。
(9)Al:0.10%以下(0%を含まない)
AlはNをAlNとして固定し、固溶Nによる靭性劣化を抑制する上、組織微細化して靭性向上に寄与する。この効果を発揮させるには0.001%以上添加すればよい。しかしながら、AlはSiと同様に焼戻し時のセメンタイト析出を抑制し、残留γを増加させる効果があり、Al増量すると残留γの増加によりばね特性が劣化する。このため、0.10%以下とする必要がる。
(10)V:1.0%以下(0%を含まない)
Vは炭窒化物を形成して組織微細化に寄与し、靭性向上に有効である。この効果を発揮させるには、0.020%以上添加すればよい。しかしながら、過剰添加は炭窒化物が粗大化し靭性を劣化させる。この観点から1.0%以下とする必要がある。更に、コスト低減の観点からは必要最小限の添加が望ましい。
(11)Ti:0.30%以下 (0%を含まない)
Tiは炭窒化物を形成して組織微細化に寄与し、靭性向上に有効である。この効果を発揮させるには、0.020%以上添加すればよい。しかしながら、過剰添加は炭窒化物が粗大化し靭性を劣化させる。この観点から0.30%以下とする必要がある。更に、コスト低減の観点からは必要最小限の添加が望ましい。
(12)Nb:0.30%以下(0%を含まない)
Nbは炭窒化物を形成して組織微細化に寄与し、靭性向上に有効である。この効果を発揮させるには、0.02%以上添加すればよい。しかしながら、過剰添加は炭窒化物が粗大化し靭性を劣化させる。この観点から0.30%以下とする必要がある。更に、コスト低減の観点からは必要最小限の添加が望ましい。
(13)Ni:3.0 %以下(0%を含まない)
Niは添加によって靭性を向上させることが知られており、また、加熱時の脱炭を抑制する効果もあり、ばね耐久特性向上に寄与する。これらの効果を発揮させるには0.1%以上添加すればよい。一方、過剰添加すると残留γを増加させてばね特性を劣化させる。よって、3.0%以下とする必要がある。更に、コスト低減の観点からは必要最小限の添加が望ましい。
(14)Cu:3.0%以下(0%を含まない)
Cuは加熱時の脱炭を抑制する効果があり、ばね耐久特性向上に寄与する。この効果を発揮させるには0.10%以上添加すればよい。一方、過剰添加すると残留γを増加させてばね特性を劣化させる。よって、3.0%以下とする必要がある。更に、コスト低減の観点からは必要最小限の添加が望ましい。
(15)Mo:2.0%以下(0%を含まない)
MoはPの粒界偏析を軽減し、靭性劣化を抑制する効果がある。また、炭化物を形成して組織微細化に寄与し、靭性を向上させる。これらの効果を発現させるには0.2%以上の添加が必要である。一方、過剰添加すると顕著な凝固偏析帯を形成し、靭性劣化を招く。よって2.0%以下とする必要がある。更に、コスト低減の観点からは必要最小限の添加が望ましい。
(16)Ca:0.0050%以下(0%を含まない)
Caは微量添加で硫化物を微細化し、靭性向上に寄与する。この効果を発現するためには、0.0001%以上添加すればよい。一方、過剰添加すると逆に靭性劣化を招く。よって、0.0050%以下とする必要がある。
(17)Mg: 0.0050%以下(0%を含まない)
Mgは微量添加で硫化物を微細化し、靭性向上に寄与する。この効果を発現するためには、0.0001%以上添加すればよい。一方、過剰添加すると逆に靭性劣化を招く。よって0.0050%以下とする必要がある。
(18)REM:0.020%以下(0%を含まない)
REMは微量添加で硫化物を微細化し、靭性向上に寄与する。この効果を発現するためには、0.0001%以上添加すればよい。一方、過剰添加すると逆に靭性劣化を招く。よって、0.020%以下とする必要がある。
(19)Zr: 0.10%以下(0%を含まない)
Zrは炭窒化物を形成して組織微細化に寄与し、靭性向上に有効である。この効果を発揮させるには、0.010%以上添加すればよい。しかしながら、過剰添加は炭窒化物が粗大化し靭性を劣化させる。この観点から0.10%以下とする必要がある。更に、コスト低減の観点からは必要最小限の添加が望ましい。
(20)Ta:0.10%以下(0%を含まない)
Taは炭窒化物を形成して組織微細化に寄与し、靭性向上に有効である。この効果を発揮させるには、0.01%以上添加すればよい。しかしながら、過剰添加は炭窒化物が粗大化し靭性を劣化させる。この観点から0.10%以下とする必要がある。更に、コスト低減の観点からは必要最小限の添加が望ましい。
(21)Hf:0.10%以下(0%を含まない)
Hfは炭窒化物を形成して組織微細化に寄与し、靭性向上に有効である。この効果を発揮させるには、0.010%以上添加すればよい。しかしながら、過剰添加は炭窒化物が粗大化し靭性を劣化させる。この観点から0.10%以下とする必要がある。更に、コスト低減の観点からは必要最小限の添加が望ましい。
〔3〕実施例
本発明の効果を検証するため下記の実験を実施した。
(1)シームレス鋼管の製造
表1に示す成分を有する、外径143mm、肉厚50mmの各鋼管ビレットを1000℃に加熱して熱間静水圧装置により熱間加工して、外径60mm、肉厚15mmの素管とし、さらにこれを抽伸機により冷間加工して外径16mm、肉厚4mmの鋼管を作製した。これらの鋼管を表2に示すように700~950℃の温度(焼鈍温度)で最終焼鈍を施し、酸洗などの精製処理を行って製品のシームレス鋼管を得た。なお、最終焼鈍における冷却は空冷により行い、その冷却速度は1.5℃/sとした。
(2)鋼管の炭化物サイズの評価
上記で得られた各シームレス鋼管をその任意の横断面を観察面とするように、切断、樹脂埋め込みし、湿式研磨を施し、鏡面に仕上げた。その後、ピクラールでエッチングし、SEMを用いて金属組織観察を行った。観察位置は、パイプ肉厚中央部(t/2位置)とし、3000~5000倍にて5視野撮影した。観察写真を画像処理して、金属組織中の炭化物(セメンタイト)を円相当近似し、その最大値を求めた。この値を炭化物のサイズとして表2に記載した。
(3)鋼管の焼入れ処理
鋼管を中空ばねとした場合の特性を把握するため、上記各シームレス鋼管の焼入れ処理(焼入れ、焼戻し)を行った。焼入れは高周波加熱により1000~1150℃に加熱し、10秒間保持後に水冷した。また、焼戻しは電気炉を用いて400℃で60分間保持後空冷した。
(4)鋼管の焼入れ処理後の耐久試験
上記焼入れ処理を行った各シームレス鋼管を、最大負荷応力1150MPaおよび1200MPaにて大気耐久試験を実施した。寿命10万回以上を合格ラインとした上で、10万回未満を×(不合格)、10万回以上30万回未満を△(合格)、30万回以上50万回未満を○(合格)、50万回以上を◎(合格)として評価した。この耐久試験の結果を表2に示した。
(5)焼入れ処理後の旧オーステナイト粒径調査
前記焼入れ処理後における各シームレス鋼管の任意の横断面を観察面とするように、切断、樹脂埋め込みし、湿式研磨を施し、鏡面に仕上げた。その後、ピクリン酸飽和水溶液を用いてエッチングして旧オーステナイト粒界を現出させ、光学顕微鏡を用いて観察した。観察位置は、パイプ肉厚中央部(t/2位置)とし、400倍にて5視野撮影した。観察写真から切断法にて旧オーステナイト粒径の平均値を求めた。この旧オーステナイト粒径の値を表2に示した。
(6)焼入れ処理後の未固溶炭化物の調査
焼入れ処理後における各シームレス鋼管をその任意の横断面を観察面とするように、切断、樹脂埋め込みし、湿式研磨を施し、鏡面に仕上げた。その後、ピクラールでエッチングし、SEMを用いて金属組織観察を行ない、未固溶の炭化物の有無を調査した。この結果についても同様に表2に示した。
本出願は、2010年3月4日出願の日本特許出願(特願2010-047648)に基づくものであり、その内容はここに参照として取り込まれる。
Claims (2)
- C:0.20~0.70質量%、Si:0.5~3.0質量%、Mn:0.1~3.0質量%、P:0.030質量%以下(0%を含む)、S:0.030質量%以下(0%を含む)、N:0.02質量%以下(0%を含む)、残部Fe及び不可避的不純物からなり、炭化物が円相当径で1.00μm以下であることを特徴とする高強度中空ばね用シームレス鋼管。
- さらに、Cr:3.0質量%以下(0%を含まない、以下同じ)、B:0.0150質量%以下、Al:0.10質量%以下、V:1.0質量%以下、Ti:0.30質量%以下、Nb::0.30質量%以下、Ni:3.0質量%以下、Cu:3.0質量%以下、Mo:2.0質量%以下、Ca:0.0050質量%以下、Mg:0.0050質量%以下、REM:0.020質量%以下、Zr:0.10質量%以下、Ta:0.10質量%以下、Hf:0.10質量%以下から選ばれる1種以上を含有する請求項1に記載の高強度中空ばね用シームレス鋼管。
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Also Published As
Publication number | Publication date |
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KR101267742B1 (ko) | 2013-05-27 |
KR20120101603A (ko) | 2012-09-13 |
JP5476597B2 (ja) | 2014-04-23 |
EP2543747A4 (en) | 2014-12-31 |
CN104975224A (zh) | 2015-10-14 |
US20120325364A1 (en) | 2012-12-27 |
EP2543747A1 (en) | 2013-01-09 |
JP2011184704A (ja) | 2011-09-22 |
EP2543747B1 (en) | 2017-06-14 |
CN102741444A (zh) | 2012-10-17 |
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