WO2013018893A1 - Untempered steel for hot casting, hot-casted untempered article and method for producing same - Google Patents
Untempered steel for hot casting, hot-casted untempered article and method for producing same Download PDFInfo
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- WO2013018893A1 WO2013018893A1 PCT/JP2012/069861 JP2012069861W WO2013018893A1 WO 2013018893 A1 WO2013018893 A1 WO 2013018893A1 JP 2012069861 W JP2012069861 W JP 2012069861W WO 2013018893 A1 WO2013018893 A1 WO 2013018893A1
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21J—FORGING; HAMMERING; PRESSING METAL; RIVETING; FORGE FURNACES
- B21J1/00—Preparing metal stock or similar ancillary operations prior, during or post forging, e.g. heating or cooling
- B21J1/06—Heating or cooling methods or arrangements specially adapted for performing forging or pressing operations
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21J—FORGING; HAMMERING; PRESSING METAL; RIVETING; FORGE FURNACES
- B21J1/00—Preparing metal stock or similar ancillary operations prior, during or post forging, e.g. heating or cooling
- B21J1/003—Selecting material
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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
- C21D1/06—Surface hardening
- C21D1/09—Surface hardening by direct application of electrical or wave energy; by particle radiation
- C21D1/10—Surface hardening by direct application of electrical or wave energy; by particle radiation by electric induction
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/06—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires
- C21D8/065—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires of ferrous alloys
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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
- C21D9/30—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for crankshafts; for camshafts
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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
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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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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- 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
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur
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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
- C21D2211/002—Bainite
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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
- C21D2211/004—Dispersions; Precipitations
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/06—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires
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- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
- Y02P10/00—Technologies related to metal processing
- Y02P10/25—Process efficiency
Definitions
- the present invention relates to a non-heat treated steel material for hot forging that is processed into machine parts such as automobiles and industrial machines without being subjected to a tempering treatment after hot forging, and a hot work using the same.
- the present invention relates to a forged non-tempered product and a method for producing the same, and is particularly hot forged, has a high strength and a high durability ratio without being tempered, and can be induction hardened.
- Patent Document 1 has a strength and low temperature toughness that are higher than those of conventional tempered materials while still being hot forged, using a steel material to which Si is added in excess of 1.0% and a large amount of S, V, and N are added. It is described that hot forged non-tempered steel was obtained. However, there is no description regarding the fatigue strength and durability ratio of this non-heat treated steel.
- Non-heat treated steel for induction hardening There have been some reports on non-heat treated steel for induction hardening.
- the invention described in Patent Document 2 prevents a decrease in surface layer hardness and surface hardened layer depth due to generation of residual ferrite after induction hardening by setting the structure before induction hardening to a bainite ratio of 75% or more. It is an invention.
- the non-heat treated steel for induction hardening described in Patent Document 2 has no description regarding fatigue strength and durability ratio, and these characteristics are not considered at all.
- the invention described in Patent Document 3 is an invention that reduces the amount of retained austenite after induction hardening.
- the non-heat treated steel for induction hardening described in Patent Document 3 there is no description regarding fatigue strength and durability ratio, and these characteristics are not considered at all.
- an appropriate amount of S, Pb, Bi, Te, Se, and Ca may be added to improve machinability.
- the tensile strength is 1100 MPa or more, the machinability is improved. The effect is known to be small.
- Patent Document 4 describes an invention in which the improvement in strength after hot forging is suppressed to ensure machinability, and the fatigue strength of the entire component is improved by increasing the depth of the surface hardened layer by induction hardening. Has been.
- Patent Document 5 proposes that it is effective to reduce the high-carbon island-like martensite and retained austenite in the bainite-based metal structure.
- the durability ratio is at most 0.56 or less, and there is a limit to increasing the strength without reducing the machinability, and these fatigue strengths are both low.
- Patent Document 6 describes a crankshaft that can achieve high wear resistance and fatigue strength, and that achieves both high machinability and a method for manufacturing the crankshaft.
- the microstructure of the hot forged product before soft nitriding is made to be a bainite-based (70% or more) microstructure, and this hot forged product is soft nitrided under a temperature condition of 550 to 650 ° C.
- the mechanical properties such as fatigue strength of the crankshaft are improved.
- the steel material components are obtained using the parameters Hg representing the amounts of C, Si, Mn, Cr, Mo and V of the steel material with specific relational expressions. Is stipulated.
- nitrocarburizing treatment usually requires exposure to an atmosphere containing nitrogen and heating in a temperature range below the austenitizing temperature. Compared with surface hardening treatment by induction hardening, the equipment and cost are reduced. It takes. In addition, because the steel material intended for soft nitriding over a certain time has a large amount of Si, in the induction hardening by instantaneous induction heating only on the surface, residual austenite remains in the internal structure, and high fatigue strength is I can't get it.
- the present invention advantageously solves the above-described problems and controls the microstructure in the part by non-heat treated steel for hot forging that enables induction hardening and cooling after hot forging.
- An object of the present invention is to provide a hot forged non-heat treated product that suppresses a decrease in machinability associated with strength and improves fatigue strength, and a manufacturing method thereof.
- the present invention uses a steel in which a large amount of Mo is added to high carbon steel that can be induction hardened to obtain a high surface hardness, and in the cooling process after hot forging, a large amount of Mo carbonitride is precipitated, It has been found that it has a high durability ratio by reducing the defect density such as dislocation, and suppresses the deterioration of machinability associated with high strength, and obtains a hot forged non-heat treated product with improved fatigue strength, The present invention has been completed.
- “carbonitride” used in the present specification means carbonitride and carbide.
- the gist of the present invention is as follows.
- the steel component according to the above (1) or (2) is included, the steel structure is an area ratio of 95% or more is a bainite structure, and the average size of Mo carbonitride dispersed in the steel is 4 nm.
- a hot-forged non-tempered product capable of induction hardening characterized by being 11 nm or less.
- the steel material comprising the component composition described in (1) or (2) above is heated to 1000 ° C. or more and 1250 ° C. or less for hot forging, and after the hot forging, the average cooling rate up to 200 ° C. Is heated at 0.05 ° C./second or more and 0.80 ° C./second or less, and induction hardening is performed on a portion where strength is required.
- the steel of the present invention is optimal as a raw material for hot forged non-heat treated steel parts capable of induction hardening with high fatigue strength while suppressing an increase in cutting cost.
- the manufacturing method of this invention can manufacture the hot forging non-tempered goods which can be induction-hardened which has a high durability ratio and high fatigue strength.
- the hot forged non-heat treated product of the present invention can be induction hardened when used as a part for automobiles or industrial machines, so that the parts can be further strengthened, and the weight of the vehicle can be reduced. Contributes to reducing fuel consumption and cost.
- the present invention has been made for the first time after further studies based on these findings.
- C 0.45 to 0.60% C is an important element that determines the strength of steel. Compared to other alloy elements, the alloy cost is low. If a large amount of C can be added, the alloy cost of the steel material can be reduced. Further, the surface hardness after induction hardening is determined by the amount of C in the steel, and in order to obtain the required strength, the lower limit is made 0.45%. However, when a large amount of C is added, residual austenite or island martensite in which C is concentrated at the boundary of the lath during bainite transformation is formed and the durability ratio is lowered, so the upper limit is made 0.60%.
- the steel which can be induction-hardened of the present invention is steel that can have a surface hardness after the induction-hardening treatment that is higher than the required strength. Therefore, in the present invention, it is steel having a C content of 0.45% or more. In order to obtain higher strength, an amount of C exceeding 0.5% is preferable.
- Si 0.02 to 0.15% Si is an element that increases the amount of retained austenite in steel by bainite transformation in the cooling process after hot forging.
- Si content exceeds 0.15%, the fatigue strength and the durability ratio are significantly reduced. Therefore, the amount is limited to 0.15% or less. However, if the content is suppressed to less than 0.02%, the manufacturing cost becomes great, so the lower limit is made 0.02%.
- Mn 1.50 to 3.00%
- Mn is an element that promotes bainite transformation, and is an important element for making the structure bainite in the cooling process after hot forging. Furthermore, it combines with S to form sulfides and has the effect of improving machinability. In order to exert these effects, the lower limit is made 1.50%. On the other hand, if an amount of Mn exceeding 3.00 is added, the hardness of the substrate increases and becomes brittle, so that the machinability is significantly lowered.
- the upper limit is 3.00. In particular, an amount of Mn exceeding 2.0% is preferable because a bainite structure with an area ratio of 95% is obtained even at a low cooling rate.
- P 0.0002 to 0.150% Since P usually contains 0.0002% or more as an inevitable impurity in steel, the lower limit is made 0.0002% or more. When P is added in a large amount, P segregates at the grain boundaries of prior austenite and promotes cracking after induction hardening, so the upper limit is made 0.150%. Preferably it is 0.100% or less, More preferably, it is 0.050% or less.
- S 0.001 to 0.200%
- S forms sulfides with Mn and has an effect of improving machinability, and in order to exert the effect, the lower limit is made 0.001%.
- S forms sulfides with Mn and has an effect of improving machinability, and also has an effect of suppressing the growth of austenite grains and maintaining high toughness. In order to exert these effects, the lower limit is made 0.001%.
- the upper limit is made 0.200%.
- Cr 0.02 to 1.00% Cr, like Mn, is an element effective for promoting the bainite transformation, and in order to exert its effect, the lower limit is made 0.02%. However, if a large amount of Cr is added, the Fe-based carbide is stabilized and the surface hardness when induction hardening is reduced, so the upper limit is made 1.00%.
- Al 0.001 to 0.300%
- Al precipitates and disperses in the steel as a nitride, thereby preventing the austenite structure from coarsening during forging reheating and preventing the subsequent bainite structure from becoming coarse.
- Al combines with oxygen during machining, adheres to the tool surface, and is effective in preventing tool wear.
- the lower limit is made 0.001%.
- it is 0.050% or more, more preferably 0.100%.
- the upper limit is set to 0.300%.
- V 0.01 to 0.30%
- V is an element effective for promoting the bainite transformation, and is an element effective for forming a carbonitride, strengthening the precipitation of the bainite structure, and increasing the strength and durability ratio.
- a content of 0.01% or more is necessary.
- the upper limit is made 0.30%.
- Mo 0.03-1.00%
- Mo is not only an element effective for promoting bainite transformation, but also has the highest solid solubility in austenite compared to alloy elements such as V, Ti, Nb, etc., which can provide precipitation strengthening due to alloy carbide, and in the cooling process A large amount of Mo carbonitride is obtained.
- precipitation of carbonitride such as Mo used for precipitation strengthening is not preferable because not only fatigue strength but also tensile strength is increased and machinability is remarkably lowered.
- the size of Mo carbonitride is controlled to 4 nm or more and 11 nm or less, only the fatigue strength can be increased without increasing the tensile strength affecting the machinability, that is, the fatigue strength and the durability ratio are increased. I understood it. In order to exhibit this effect, a content of 0.03% or more is necessary. On the other hand, if it exceeds 1.00%, the effect is saturated, so the upper limit is made 1.00%.
- N 0.0020 to 0.0070% N is generally used to form a nitride with V to prevent coarsening of the austenite structure during hot forging, but V nitride serves as the nucleus of pro-eutectoid ferrite. The transformation is promoted to reduce the strength and durability ratio.
- the upper limit of the N amount is set to 0.0070%.
- the lower limit is made 0.0020%.
- Ca, Te, Zr containing one or more of Ca: 0.0002 to 0.0100%, Te: 0.0002 to 0.1000%, Zr: 0.0002 to 0.2000% are: All of them have an effect of forming oxides, becoming crystallization nuclei of Mn sulfide, and uniformly and finely dispersing Mn sulfide. In addition, any element dissolves in Mn sulfide, reduces its deformability, suppresses elongation of Mn sulfide shape after rolling or hot forging, and reduces the anisotropy of mechanical properties There is. In order to exert these effects, the lower limits of Ca, Te, and Zr are each 0.0002%.
- the structure is defined as a bainite structure with an area ratio of 95% or more. If the main structure is a bainite structure, it has a high durability ratio, but the remaining structure is ferrite, residual austenite, or island martensite. This is because the durability ratio is significantly reduced when the content is 5% or more. The fewer these remaining structures are, the higher the durability ratio is, and the area ratio is preferably 97% or more.
- the average size of Mo carbonitride dispersed in steel is 4 nm or more and 11 nm or less
- the reason why the average size of Mo carbonitrides in the bainite structure is specified to be 4 nm or more is that when the average size is less than 4 nm, the fatigue strength is high but the tensile strength is also high and the durability ratio is small. This is because it is impossible to achieve both fatigue strength and machinability. More preferably, the average size is 8 nm or more.
- the upper limit value of the average size of Mo carbonitride is defined as 11 nm because when the average size exceeds 11 nm, not only the tensile strength but also the fatigue strength is remarkably lowered, so that high fatigue strength cannot be achieved.
- the shape of Mo carbonitride is acicular and the size of Mo carbonitride used in this specification is the length in the longitudinal direction.
- Step is heated to 1000 ° C or lower and 1250 ° C or higher
- the reason why the steel material having the above-described component composition is heated to 1000 ° C. or lower and 1250 ° C. or higher is to sufficiently precipitate carbonitrides of Mo and V in the cooling process, before hot forging. This is because Mo and V are sufficiently dissolved in the steel by heating. If the heating temperature is less than 1000 ° C., Mo and V cannot be sufficiently dissolved in the steel, the precipitation strengthening amount in the subsequent cooling process is small, and the fatigue strength and durability ratio are small. On the other hand, raising the heating temperature more than necessary promotes the growth of austenite grains, and the structure transformed in the subsequent cooling process becomes coarse, and the durability ratio decreases. Therefore, the upper limit of the heating temperature is 1250 ° C.
- the average cooling rate is 0.05 ° C / second or more and 0.80 ° C / second or less to 200 ° C or less
- the average cooling rate up to 200 ° C or less is specified to be 0.05 ° C / second or more and 0.80 ° C / second or less because the time staying in the temperature range where Mo carbonitride precipitates is lengthened. This is because the precipitation amount is increased in the cooling process and the carbonitride size is controlled.
- the average cooling rate is 0.80 ° C./second or more, the precipitation amount of Mo carbonized vagina is not sufficiently obtained, and the effect of improving the strength and the durability ratio is small.
- an average cooling rate of 0.50 ° C./second or less is desirable. More preferably, it is 0.30 ° C./second or less.
- the average cooling rate is less than 0.05 ° C./second, proeutectoid ferrite having an area ratio of 5% or more is generated at the bainite lath boundary, and the fatigue strength and the durability ratio are significantly reduced.
- the present invention provides a hot forged non-tempered product capable of induction hardening with high fatigue strength, it is desirable that the tensile strength be 1300 MPa or less in order to ensure sufficient machinability. .
- a JIS Z 2201 No. 14 tensile test piece and a JIS Z 2274 No. 1 bending bending fatigue test piece were sampled from the center of these forgings, and the tensile strength and fatigue strength were determined.
- the fatigue strength was defined as the stress amplitude that did not break in 10 7 rotations in the rotating bending fatigue test.
- the ratio of the obtained fatigue strength and tensile strength was obtained as the durability ratio (fatigue strength / tensile strength).
- tissue observation was extract
- the area ratio of bainite is determined by polishing the specimen until it becomes a mirror surface, then performing repeller etching, and confirming the microstructure of proeutectoid ferrite, residual austenite, island martensite, and the like other than bainite.
- the microphotographs were taken by 10 fields of view and then calculated by image analysis.
- the average size of the Mo carbonitride was observed in 10 views of 15,000-fold transmission electron micrographs taken with a transmission electron microscope after finishing the test piece into a thin film by electrolytic polishing.
- the length in the longitudinal direction of the Mo carbonitride was determined by image analysis, and the average value was determined.
- Each of the present invention steels 1 to 18 has a bainite structure of 95% or more in area ratio, the average size of Mo carbonitride is 4.6 nm or more and 10.8 nm or less, and the durability ratio is 0.58 or more. Has a high durability ratio.
- the tensile strength is 1300 MPa or less, but as is apparent when compared with the comparable tensile strength, the conventional example No. Higher fatigue strength is achieved than tempered steel of 28 carbon steel.
- Comparative Example No. Nos. 23, 24 and 27 have a high content of either C, Si or N. 21 is within the specified steel composition range, but the average cooling rate is not specified, the amount of the remainder such as ferrite and residual austenite is large at the bainite lath boundary, and the average size of Mo carbonitride is not specified, Low strength and durability ratio.
- No. Nos. 19 and 22 have steel compositions or heat treatment conditions that are not specified, and sufficient precipitation strengthening cannot be obtained, resulting in a low durability ratio. No. Since the heating temperature of No. 20 was increased more than necessary, the bainite structure was coarsened, and the durability ratio was rather low.
- No. No. 25 has Mn added more than necessary, has high tensile strength, and is very difficult to cut. On the other hand, no. In No. 26, Al is added more than necessary, and the fatigue strength and durability ratio are lowered.
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Abstract
Description
(a)面積率で95%以上のベイナイト組織中に、微細なMo炭窒化物を分散させることによって、従来の非調質鋼より高い耐久比(=疲労強度/引張強さ)を有する。熱間鍛造後の冷却速度の影響が大きく、冷却速度が小さいほど耐久比は向上する。これは、冷却速度が小さいほどMo炭窒化物が析出する温度域にとどまる時間が長くなり析出量が増えることによって、引張強さおよび疲労強度は上昇するが、冷却速度が小さければ小さいほど、その炭窒化物は粗大化し引張強さは顕著に低下する一方、疲労強度は低下することなく上昇または維持するためである。一般的に析出強化に用いられるMo等の炭窒化物の析出は、疲労強度だけでなく引張強度も上昇し、被削性を著しく低下するため高疲労強度化と良被削性は両立しない。析出物を粗大化し、Mo炭窒化物のサイズを4nm以上、11nm以下に制御することによって、被削性に影響を及ぼす引張強さは上げずに疲労強度を高めることができることがわかった。ただし、主体組織をベイナイト組織とし、それ以外の初析フェライトや残留オーステナイト組織を面積率5%未満にする必要がある。
(b)VはMoと同様に、炭窒化物を形成し耐久比向上に寄与するものの、高Nではより高温で安定なV窒化物を形成し、熱間鍛造後の冷却過程で初析フェライトの核となり、強度および耐久比の低下につながる。V炭窒化物による耐久比向上の効果を十分に利用するには低Nが必要条件である。 The present inventors diligently studied the steel component range, the structure morphology, and the heat treatment conditions for the above-mentioned objects, and found the following findings. That is,
(A) It has a higher durability ratio (= fatigue strength / tensile strength) than conventional non-tempered steel by dispersing fine Mo carbonitrides in a bainite structure of 95% or more in area ratio. The influence of the cooling rate after hot forging is large, and the durability ratio is improved as the cooling rate is decreased. This is because the tensile strength and fatigue strength increase as the cooling rate decreases and the amount of precipitation increases as the time in which the Mo carbonitride precipitates increases, but the smaller the cooling rate, the more This is because the carbonitride is coarsened and the tensile strength is remarkably reduced, while the fatigue strength is increased or maintained without decreasing. In general, precipitation of carbonitride such as Mo used for precipitation strengthening increases not only fatigue strength but also tensile strength and remarkably reduces machinability, so that high fatigue strength and good machinability are not compatible. It was found that fatigue strength can be increased without increasing the tensile strength affecting machinability by coarsening the precipitate and controlling the size of the Mo carbonitride to 4 nm or more and 11 nm or less. However, it is necessary that the main structure is a bainite structure and the other pro-eutectoid ferrite and retained austenite structure is less than 5%.
(B) V, like Mo, forms carbonitrides and contributes to improving the durability ratio. However, high N forms V nitrides that are stable at higher temperatures, and proeutectoid ferrite in the cooling process after hot forging. It leads to a decrease in strength and durability ratio. Low N is a necessary condition for fully utilizing the effect of improving the durability ratio by V carbonitride.
Cは鋼の強度を決める重要な元素である。他の合金元素に比べて合金コストは安く、Cを多量に添加することができれば鋼材の合金コストは低減できる。また高周波焼入れ処理した後の表面硬さは鋼中のC量で決まり必要強度を得るためには、下限を0.45%とする。しかしながら、多量のCを添加すると、ベイナイト変態時にラスの境界にCが濃縮した残留オーステナイトや島状マルテンサイトが生成し、耐久比が低下するため、上限は0.60%とする。なお、本発明の高周波焼入れ処理が可能な鋼とは、高周波焼入れ処理した後の表面硬さが要求される強度以上になりうる鋼のことである。したがって、本発明において、0.45%以上のC量を有する鋼のことである。より高い強度を得るには、0.5%を超えるC量が好ましい。 C: 0.45 to 0.60%
C is an important element that determines the strength of steel. Compared to other alloy elements, the alloy cost is low. If a large amount of C can be added, the alloy cost of the steel material can be reduced. Further, the surface hardness after induction hardening is determined by the amount of C in the steel, and in order to obtain the required strength, the lower limit is made 0.45%. However, when a large amount of C is added, residual austenite or island martensite in which C is concentrated at the boundary of the lath during bainite transformation is formed and the durability ratio is lowered, so the upper limit is made 0.60%. In addition, the steel which can be induction-hardened of the present invention is steel that can have a surface hardness after the induction-hardening treatment that is higher than the required strength. Therefore, in the present invention, it is steel having a C content of 0.45% or more. In order to obtain higher strength, an amount of C exceeding 0.5% is preferable.
Siは、熱間鍛造後の冷却過程におけるベイナイト変態で、鋼中に残留オーステナイト量を増加させる元素である。表層のみ加熱する高周波焼入れ処理を施す場合、非加熱部では残留オーステナイトが残存し、Si量が0.15%を超えると疲労強度、耐久比は顕著に低下する。したがって、その量を0.15%以下に制限する。しかし、0.02%未満に抑制すると製造コストが多大なものとなるため、下限を0.02%とする。 Si: 0.02 to 0.15%
Si is an element that increases the amount of retained austenite in steel by bainite transformation in the cooling process after hot forging. When an induction hardening process for heating only the surface layer is performed, residual austenite remains in the non-heated part, and when the Si content exceeds 0.15%, the fatigue strength and the durability ratio are significantly reduced. Therefore, the amount is limited to 0.15% or less. However, if the content is suppressed to less than 0.02%, the manufacturing cost becomes great, so the lower limit is made 0.02%.
Mnはベイナイト変態を促進する元素であり、熱間鍛造後の冷却過程で組織をベイナイトとするために重要な元素である。さらにSと結合して硫化物を形成し、被削性を向上させる効果がある。これら効果を発揮するためには、下限は1.50%とする。一方、3.00超のMn量を添加すると素地の硬さが大きくなり脆くなるため、かえって被削性が顕著に低下する。上限は3.00とする。特に、2.0%を超えるMn量は、遅い冷却速度においても面積率で95%のベイナイト組織となるので、好ましい。 Mn: 1.50 to 3.00%
Mn is an element that promotes bainite transformation, and is an important element for making the structure bainite in the cooling process after hot forging. Furthermore, it combines with S to form sulfides and has the effect of improving machinability. In order to exert these effects, the lower limit is made 1.50%. On the other hand, if an amount of Mn exceeding 3.00 is added, the hardness of the substrate increases and becomes brittle, so that the machinability is significantly lowered. The upper limit is 3.00. In particular, an amount of Mn exceeding 2.0% is preferable because a bainite structure with an area ratio of 95% is obtained even at a low cooling rate.
Pは鋼中に不可避的不純物として通常、0.0002%以上は含有しているため、下限を0.0002%以上とする。多量に添加すると、Pは旧オーステナイトの粒界等に偏析し、高周波焼入れ後の割れを助長する元素であるため、上限は0.150%とする。好ましくは0.100%以下であり、より好ましくは0.050%以下である。 P: 0.0002 to 0.150%
Since P usually contains 0.0002% or more as an inevitable impurity in steel, the lower limit is made 0.0002% or more. When P is added in a large amount, P segregates at the grain boundaries of prior austenite and promotes cracking after induction hardening, so the upper limit is made 0.150%. Preferably it is 0.100% or less, More preferably, it is 0.050% or less.
SはMnと硫化物を形成し、被削性を向上させる効果があり、その効果を発揮するためには、下限を0.001%とする。SはMnと硫化物を形成し、被削性を向上させる効果があり、またオーステナイト粒の成長を抑制し高靱性を維持する効果もある。これら効果を発揮するためには、下限は0.001%とする。しかし、Mn量にも依存するが、多量に添加すると機械的性質に異方性が大きくなることから、上限は0.200%とする。 S: 0.001 to 0.200%
S forms sulfides with Mn and has an effect of improving machinability, and in order to exert the effect, the lower limit is made 0.001%. S forms sulfides with Mn and has an effect of improving machinability, and also has an effect of suppressing the growth of austenite grains and maintaining high toughness. In order to exert these effects, the lower limit is made 0.001%. However, although depending on the amount of Mn, since anisotropy increases in mechanical properties when added in a large amount, the upper limit is made 0.200%.
CrはMnと同様にベイナイト変態を促進するのに有効な元素であり、その効果を発揮するためには、下限を0.02%とする。しかしながら、Crを多量に添加すると、Fe系炭化物を安定化させ、高周波焼入れした場合の表面硬さが低下することから、上限は1.00%とする。 Cr: 0.02 to 1.00%
Cr, like Mn, is an element effective for promoting the bainite transformation, and in order to exert its effect, the lower limit is made 0.02%. However, if a large amount of Cr is added, the Fe-based carbide is stabilized and the surface hardness when induction hardening is reduced, so the upper limit is made 1.00%.
Alは窒化物として鋼中に析出分散することにより、鍛造再加熱時のオーステナイト組織の粗大化を防止し、その後のベイナイト組織の粗大化も防止する効果がある。さらにAlは機械加工時に酸素と結合して工具面に付着し、工具摩耗の防止に効果がある。これら効果を発揮するためには、下限は0.001%とする。好ましくは、0.050%以上とし、より好ましくは0.100%とする。一方、0.300%超では多量の硬質介在物を形成し耐久比および被削性のいずれも低下する。したがって、上限は0.300%とする。 Al: 0.001 to 0.300%
Al precipitates and disperses in the steel as a nitride, thereby preventing the austenite structure from coarsening during forging reheating and preventing the subsequent bainite structure from becoming coarse. Furthermore, Al combines with oxygen during machining, adheres to the tool surface, and is effective in preventing tool wear. In order to exert these effects, the lower limit is made 0.001%. Preferably, it is 0.050% or more, more preferably 0.100%. On the other hand, if it exceeds 0.300%, a large amount of hard inclusions are formed, and both the durability ratio and the machinability are lowered. Therefore, the upper limit is set to 0.300%.
Vはベイナイト変態を促進するのに有効な元素であり、また炭窒化物を形成し、ベイナイト組織を析出強化し強度、および耐久比を高めるのに有効な元素である。この効果を発揮するには0.01%以上の含有量が必要である。一方、0.30%を超えると、その効果は飽和するため、上限は0.30%とする。 V: 0.01 to 0.30%
V is an element effective for promoting the bainite transformation, and is an element effective for forming a carbonitride, strengthening the precipitation of the bainite structure, and increasing the strength and durability ratio. In order to exhibit this effect, a content of 0.01% or more is necessary. On the other hand, if it exceeds 0.30%, the effect is saturated, so the upper limit is made 0.30%.
Moはベイナイト変態を促進するのに有効な元素だけでなく、合金炭化物による析出強化が得られるV、TiやNb等の合金元素に比べて、オーステナイト中の固溶度が最も大きく、冷却過程においてMo炭窒化物の大きな析出量が得られる。一般的に析出強化に用いられるMo等の炭窒化物の析出は疲労強度だけでなく、引張強さも上昇し被削性を著しく低下させるため好ましくない。しかし、Mo炭窒化物のサイズが4nm以上、11nm以下に制御すると、被削性に影響を及ぼす引張強さは上げずに疲労強度のみ上げることができ、つまり、疲労強度、および耐久比を高めることがわかった。この効果を発揮するには0.03%以上の含有量が必要である。一方、1.00%を超えると、その効果は飽和するため、上限を1.00%とする。 Mo: 0.03-1.00%
Mo is not only an element effective for promoting bainite transformation, but also has the highest solid solubility in austenite compared to alloy elements such as V, Ti, Nb, etc., which can provide precipitation strengthening due to alloy carbide, and in the cooling process A large amount of Mo carbonitride is obtained. Generally, precipitation of carbonitride such as Mo used for precipitation strengthening is not preferable because not only fatigue strength but also tensile strength is increased and machinability is remarkably lowered. However, when the size of Mo carbonitride is controlled to 4 nm or more and 11 nm or less, only the fatigue strength can be increased without increasing the tensile strength affecting the machinability, that is, the fatigue strength and the durability ratio are increased. I understood it. In order to exhibit this effect, a content of 0.03% or more is necessary. On the other hand, if it exceeds 1.00%, the effect is saturated, so the upper limit is made 1.00%.
Nは、一般的にはVと窒化物を形成して熱間鍛造時のオーステナイト組織の粗大化を防止することに利用されるが、V窒化物は初析フェライトの核となり、かえって初析フェライトの変態を促進し強度、および耐久比を低下させる。V窒化物の生成を抑制するには、N量の上限を0.0070%とする。また鋼中の不可避的不純物として通常、0.0020%以上は含有しているため、下限を0.0020%とする。 N: 0.0020 to 0.0070%
N is generally used to form a nitride with V to prevent coarsening of the austenite structure during hot forging, but V nitride serves as the nucleus of pro-eutectoid ferrite. The transformation is promoted to reduce the strength and durability ratio. In order to suppress the formation of V nitride, the upper limit of the N amount is set to 0.0070%. Moreover, since 0.0020% or more is usually contained as an inevitable impurity in steel, the lower limit is made 0.0020%.
Ca、Te、Zrはいずれも酸化物を形成し、Mn硫化物の晶出核となりMn硫化物を均一微細分散する効果がある。また、いずれの元素もMn硫化物中に固溶し、その変形能を低下させ、圧延や熱間鍛造後のMn硫化物形状の伸延を抑制し、機械的性質の異方性を小さくする効果がある。これら効果を発揮するには、Ca、Te、Zrの下限はそれぞれ0.0002%とする。一方、Caは0.0100%、Teは0.1000%、Zrは0.2000%を超えると、かえってこれら酸化物や硫化物等の硬質介在物を多量に生成し、耐久比および被削性は低下する。したがって、Caの上限は0.0100%とし、Teの上限は0.1000%とし、Zrの上限は0.2000%とする。 Ca, Te, Zr containing one or more of Ca: 0.0002 to 0.0100%, Te: 0.0002 to 0.1000%, Zr: 0.0002 to 0.2000% are: All of them have an effect of forming oxides, becoming crystallization nuclei of Mn sulfide, and uniformly and finely dispersing Mn sulfide. In addition, any element dissolves in Mn sulfide, reduces its deformability, suppresses elongation of Mn sulfide shape after rolling or hot forging, and reduces the anisotropy of mechanical properties There is. In order to exert these effects, the lower limits of Ca, Te, and Zr are each 0.0002%. On the other hand, when Ca exceeds 0.0100%, Te exceeds 0.1000%, and Zr exceeds 0.2000%, a large amount of hard inclusions such as oxides and sulfides are generated, and the durability ratio and machinability are increased. Will decline. Therefore, the upper limit of Ca is 0.0100%, the upper limit of Te is 0.1000%, and the upper limit of Zr is 0.2000%.
組織を面積率で95%以上のベイナイト組織に規定したのは、主体組織がベイナイト組織であれば高耐久比を有するものの、その残部組織であるフェライト、残留オーステナイトまたは島状マルテンサイトが面積率で5%以上からなる場合、耐久比は著しく低下するためである。これら残部組織が少なければ少ないほど、耐久比は高く、好ましくは面積率で97%以上である。 (Bainitic structure with an area ratio of 95% or more)
The structure is defined as a bainite structure with an area ratio of 95% or more. If the main structure is a bainite structure, it has a high durability ratio, but the remaining structure is ferrite, residual austenite, or island martensite. This is because the durability ratio is significantly reduced when the content is 5% or more. The fewer these remaining structures are, the higher the durability ratio is, and the area ratio is preferably 97% or more.
ベイナイト組織中のMo炭窒化物の平均サイズを4nm以上に規定したのは、その平均サイズが4nm未満では、高い疲労強度を有するが同時に引張強さも高く、耐久比の値としては小さいため、高疲労強度化と被削性の両立は実現できないからである。より好ましくはその平均サイズ8nm以上である。またMo炭窒化物の平均サイズの上限値を11nmに規定したのは、その平均サイズが11nm超では、引張強さだけでなく疲労強度も著しく低下するため高疲労強度化を達成できないからである。なお、Mo炭窒化物の形状は針状であり、本明細書で用いるMo炭窒化物のサイズは長手方向の長さである。 (The average size of Mo carbonitride dispersed in steel is 4 nm or more and 11 nm or less)
The reason why the average size of Mo carbonitrides in the bainite structure is specified to be 4 nm or more is that when the average size is less than 4 nm, the fatigue strength is high but the tensile strength is also high and the durability ratio is small. This is because it is impossible to achieve both fatigue strength and machinability. More preferably, the average size is 8 nm or more. Further, the upper limit value of the average size of Mo carbonitride is defined as 11 nm because when the average size exceeds 11 nm, not only the tensile strength but also the fatigue strength is remarkably lowered, so that high fatigue strength cannot be achieved. . In addition, the shape of Mo carbonitride is acicular and the size of Mo carbonitride used in this specification is the length in the longitudinal direction.
上述した成分組成からなる鋼材を1000℃以下、1250℃以上に加熱することを規定したのは、冷却過程でMo、Vの炭窒化物を十分に析出させることが目的で、熱間鍛造前の加熱によってMo、Vを鋼中に十分に溶体化させるためである。加熱温度1000℃未満では、Mo、Vを鋼中に十分に溶体化させることができず、その後の冷却過程での析出強化量が小さく、疲労強度、耐久比は小さくなる。一方、必要以上に加熱温度を上げることは、オーステナイト粒の成長を促し、その後の冷却過程で変態した組織が粗大となりかえって耐久比が低下する。したがって、加熱温度の上限を1250℃とする。 (Steel is heated to 1000 ° C or lower and 1250 ° C or higher)
The reason why the steel material having the above-described component composition is heated to 1000 ° C. or lower and 1250 ° C. or higher is to sufficiently precipitate carbonitrides of Mo and V in the cooling process, before hot forging. This is because Mo and V are sufficiently dissolved in the steel by heating. If the heating temperature is less than 1000 ° C., Mo and V cannot be sufficiently dissolved in the steel, the precipitation strengthening amount in the subsequent cooling process is small, and the fatigue strength and durability ratio are small. On the other hand, raising the heating temperature more than necessary promotes the growth of austenite grains, and the structure transformed in the subsequent cooling process becomes coarse, and the durability ratio decreases. Therefore, the upper limit of the heating temperature is 1250 ° C.
熱間鍛造した後、200℃以下まで平均冷却速度は0.05℃/秒以上、0.80℃/秒以下に規定したのは、Mo炭窒化物が析出する温度域にとどまる時間を長くして、冷却過程で析出量を増加させ、その炭窒化物サイズを制御するためである。平均冷却速度が0.80℃/秒以上では、Mo炭化膣物の析出量が十分得られず、強度、および耐久比向上効果が小さい。特にMo炭窒化物を粗大化し高耐久比を有するには、好ましくは平均冷却速度0.50℃/秒以下が望ましい。より好ましくは0.30℃/秒以下である。一方、平均冷却速度が0.05℃/秒未満では、ベイナイトラス境界に面積率で5%以上の初析フェライトが生成し、疲労強度、および耐久比を顕著に低下する。 (After hot forging, the average cooling rate is 0.05 ° C / second or more and 0.80 ° C / second or less to 200 ° C or less)
After hot forging, the average cooling rate up to 200 ° C or less is specified to be 0.05 ° C / second or more and 0.80 ° C / second or less because the time staying in the temperature range where Mo carbonitride precipitates is lengthened. This is because the precipitation amount is increased in the cooling process and the carbonitride size is controlled. When the average cooling rate is 0.80 ° C./second or more, the precipitation amount of Mo carbonized vagina is not sufficiently obtained, and the effect of improving the strength and the durability ratio is small. In particular, in order to coarsen Mo carbonitride and have a high durability ratio, an average cooling rate of 0.50 ° C./second or less is desirable. More preferably, it is 0.30 ° C./second or less. On the other hand, when the average cooling rate is less than 0.05 ° C./second, proeutectoid ferrite having an area ratio of 5% or more is generated at the bainite lath boundary, and the fatigue strength and the durability ratio are significantly reduced.
Claims (4)
- 質量%で、
C:0.45~0.60%、
Si:0.02~0.15%、
Mn:1.50~3.00%、
P:0.0002~0.150%、
S:0.001~0.200%、
Cr:0.02~1.00%、
Al:0.001~0.300%、
V:0.01~0.30%、
Mo:0.03~1.00%、
N:0.0020~0.0070%、
を含有し、残部がFe及び不可避不純物からなる高周波焼入れ処理が可能な熱間鍛造用非調質鋼。 % By mass
C: 0.45 to 0.60%,
Si: 0.02 to 0.15%,
Mn: 1.50 to 3.00%,
P: 0.0002 to 0.150%,
S: 0.001 to 0.200%,
Cr: 0.02 to 1.00%,
Al: 0.001 to 0.300%,
V: 0.01 to 0.30%
Mo: 0.03-1.00%,
N: 0.0020 to 0.0070%,
Non-tempered steel for hot forging, which can be induction-hardened with the balance being Fe and inevitable impurities. - さらに、質量%で、
Ca:0.0002~0.0100%、
Te:0.0002~0.1000%、
Zr:0.0002~0.2000%
のうちの1種または2種以上を含有することを特徴とする請求項1に記載の高周波焼入れ処理可能な熱間鍛造用非調質鋼。 Furthermore, in mass%,
Ca: 0.0002 to 0.0100%,
Te: 0.0002 to 0.1000%,
Zr: 0.0002 to 0.2000%
The non-tempered steel for hot forging capable of induction hardening according to claim 1, comprising one or more of them. - 請求項1または2に記載の鋼成分を有し、鋼組織が、面積率で95%以上がベイナイト組織であり、鋼中に分散したMo炭窒化物の平均サイズが4nm以上、11nm以下であることを特徴とする高周波焼入れが可能な熱間鍛造非調質品。 The steel composition according to claim 1 or 2, having a steel structure having an area ratio of 95% or more is a bainite structure, and an average size of Mo carbonitride dispersed in the steel is 4 nm or more and 11 nm or less. This is a hot forged non-tempered product that can be induction hardened.
- 請求項1または2に記載の成分組成からなる鋼材を、1000℃以上、1250℃以下に加熱して熱間鍛造し、該熱間鍛造後、200℃までにおける平均冷却速度を0.05℃/秒以上、0.80℃/秒以下で冷却し、強度が必要な部位に高周波焼入れ処理を施すことを特徴とする熱間鍛造非調質品の製造方法。 The steel material having the component composition according to claim 1 or 2 is heated to 1000 ° C. or higher and 1250 ° C. or lower and hot forged, and after the hot forging, an average cooling rate up to 200 ° C. is 0.05 ° C. / A method for producing a hot forged non-tempered product, characterized by cooling at a rate of not less than 2 seconds and not more than 0.80 ° C./second and subjecting a portion requiring strength to induction hardening.
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US20170275741A1 (en) * | 2014-09-02 | 2017-09-28 | Nippon Steel & Sumitomo Metal Corporation | Non-thermal refined nitrocarburized component |
CN112301208A (en) * | 2019-07-25 | 2021-02-02 | 广东中坤钒钢科技有限公司 | Induction heat treatment method of non-quenched and tempered steel motor shaft and motor shaft manufactured by adopting method |
JP7469643B2 (en) | 2020-05-21 | 2024-04-17 | 日本製鉄株式会社 | Steel wire, wire rods for non-tempered machine parts, and non-tempered machine parts |
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JPS61166919A (en) * | 1985-01-18 | 1986-07-28 | Nippon Steel Corp | Manufacture of unrefined warm-forged article having high toughness |
JPH06235043A (en) * | 1993-02-05 | 1994-08-23 | Aichi Steel Works Ltd | High strength non-heattreated rolled bar steel |
JPH07316720A (en) * | 1994-05-26 | 1995-12-05 | Sumitomo Metal Ind Ltd | Non-heat treated steel having high durability ratio and high strength, and its production |
JPH10298703A (en) * | 1997-04-21 | 1998-11-10 | Mitsubishi Seiko Muroran Tokushuko Kk | Bainite type high strength and high toughness non-refined steel for hot forging, excellent in yield ratio and endurance ratio |
JP2006161150A (en) * | 2004-11-09 | 2006-06-22 | Jfe Steel Kk | Carbon steel for induction hardening and component for machine structure |
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JP4507494B2 (en) * | 2003-01-17 | 2010-07-21 | Jfeスチール株式会社 | Method for producing high strength steel with excellent fatigue strength |
EP1584701B1 (en) * | 2003-01-17 | 2008-10-08 | JFE Steel Corporation | Steel product for induction hardening, induction-hardened member using the same, and methods for producing them |
JP4728204B2 (en) * | 2006-11-17 | 2011-07-20 | 株式会社神戸製鋼所 | High strength non-tempered hot forging steel with excellent fatigue limit ratio and toughness |
JP4251229B1 (en) * | 2007-09-19 | 2009-04-08 | 住友金属工業株式会社 | Low alloy steel for high pressure hydrogen gas environment and container for high pressure hydrogen |
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2012
- 2012-08-03 JP JP2012552207A patent/JP5206911B1/en active Active
- 2012-08-03 WO PCT/JP2012/069861 patent/WO2013018893A1/en active Application Filing
- 2012-08-03 CN CN201280003887.9A patent/CN103228809B/en not_active Expired - Fee Related
- 2012-08-03 KR KR1020147000580A patent/KR101458348B1/en active IP Right Grant
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JPS61166919A (en) * | 1985-01-18 | 1986-07-28 | Nippon Steel Corp | Manufacture of unrefined warm-forged article having high toughness |
JPH06235043A (en) * | 1993-02-05 | 1994-08-23 | Aichi Steel Works Ltd | High strength non-heattreated rolled bar steel |
JPH07316720A (en) * | 1994-05-26 | 1995-12-05 | Sumitomo Metal Ind Ltd | Non-heat treated steel having high durability ratio and high strength, and its production |
JPH10298703A (en) * | 1997-04-21 | 1998-11-10 | Mitsubishi Seiko Muroran Tokushuko Kk | Bainite type high strength and high toughness non-refined steel for hot forging, excellent in yield ratio and endurance ratio |
JP2006161150A (en) * | 2004-11-09 | 2006-06-22 | Jfe Steel Kk | Carbon steel for induction hardening and component for machine structure |
Cited By (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US20170275741A1 (en) * | 2014-09-02 | 2017-09-28 | Nippon Steel & Sumitomo Metal Corporation | Non-thermal refined nitrocarburized component |
CN112301208A (en) * | 2019-07-25 | 2021-02-02 | 广东中坤钒钢科技有限公司 | Induction heat treatment method of non-quenched and tempered steel motor shaft and motor shaft manufactured by adopting method |
JP7469643B2 (en) | 2020-05-21 | 2024-04-17 | 日本製鉄株式会社 | Steel wire, wire rods for non-tempered machine parts, and non-tempered machine parts |
Also Published As
Publication number | Publication date |
---|---|
JPWO2013018893A1 (en) | 2015-03-05 |
CN103228809B (en) | 2016-07-27 |
JP5206911B1 (en) | 2013-06-12 |
KR20140012209A (en) | 2014-01-29 |
CN103228809A (en) | 2013-07-31 |
KR101458348B1 (en) | 2014-11-04 |
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