CN102482743A - High-strength spring steel - Google Patents
High-strength spring steel Download PDFInfo
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- CN102482743A CN102482743A CN2010800393602A CN201080039360A CN102482743A CN 102482743 A CN102482743 A CN 102482743A CN 2010800393602 A CN2010800393602 A CN 2010800393602A CN 201080039360 A CN201080039360 A CN 201080039360A CN 102482743 A CN102482743 A CN 102482743A
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- spring
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- corrosion fatigue
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- 229910000639 Spring steel Inorganic materials 0.000 title claims abstract description 47
- 229910052799 carbon Inorganic materials 0.000 claims abstract description 23
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims abstract description 22
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims abstract description 21
- 229910052758 niobium Inorganic materials 0.000 claims abstract description 19
- 229910052720 vanadium Inorganic materials 0.000 claims abstract description 16
- 229910052742 iron Inorganic materials 0.000 claims abstract description 11
- 229910052710 silicon Inorganic materials 0.000 claims abstract description 10
- 239000012535 impurity Substances 0.000 claims abstract description 7
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 4
- 238000010791 quenching Methods 0.000 claims description 47
- 230000007797 corrosion Effects 0.000 claims description 43
- 238000005260 corrosion Methods 0.000 claims description 43
- 230000000171 quenching effect Effects 0.000 claims description 43
- 229910000831 Steel Inorganic materials 0.000 claims description 30
- 239000010959 steel Substances 0.000 claims description 30
- 229910052748 manganese Inorganic materials 0.000 claims description 10
- 238000000034 method Methods 0.000 claims description 9
- 238000012545 processing Methods 0.000 claims description 9
- 229910052802 copper Inorganic materials 0.000 claims description 8
- 238000004519 manufacturing process Methods 0.000 claims description 4
- 229910052719 titanium Inorganic materials 0.000 abstract description 13
- 229910052717 sulfur Inorganic materials 0.000 abstract description 3
- 229910052698 phosphorus Inorganic materials 0.000 abstract description 2
- 239000011651 chromium Substances 0.000 abstract 2
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 abstract 1
- OAICVXFJPJFONN-UHFFFAOYSA-N Phosphorus Chemical compound [P] OAICVXFJPJFONN-UHFFFAOYSA-N 0.000 abstract 1
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 abstract 1
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 abstract 1
- 239000011572 manganese Substances 0.000 abstract 1
- WPBNNNQJVZRUHP-UHFFFAOYSA-L manganese(2+);methyl n-[[2-(methoxycarbonylcarbamothioylamino)phenyl]carbamothioyl]carbamate;n-[2-(sulfidocarbothioylamino)ethyl]carbamodithioate Chemical compound [Mn+2].[S-]C(=S)NCCNC([S-])=S.COC(=O)NC(=S)NC1=CC=CC=C1NC(=S)NC(=O)OC WPBNNNQJVZRUHP-UHFFFAOYSA-L 0.000 abstract 1
- 239000010955 niobium Substances 0.000 abstract 1
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 abstract 1
- 239000011574 phosphorus Substances 0.000 abstract 1
- 239000010703 silicon Substances 0.000 abstract 1
- 239000011593 sulfur Substances 0.000 abstract 1
- 239000010936 titanium Substances 0.000 abstract 1
- LEONUFNNVUYDNQ-UHFFFAOYSA-N vanadium atom Chemical compound [V] LEONUFNNVUYDNQ-UHFFFAOYSA-N 0.000 abstract 1
- 238000012360 testing method Methods 0.000 description 18
- 238000005496 tempering Methods 0.000 description 17
- 230000000694 effects Effects 0.000 description 14
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 description 11
- 208000037656 Respiratory Sounds Diseases 0.000 description 11
- 238000010438 heat treatment Methods 0.000 description 11
- 229910052739 hydrogen Inorganic materials 0.000 description 11
- 239000001257 hydrogen Substances 0.000 description 11
- 230000006866 deterioration Effects 0.000 description 10
- 239000000463 material Substances 0.000 description 9
- 238000005275 alloying Methods 0.000 description 7
- 239000013078 crystal Substances 0.000 description 7
- 239000004615 ingredient Substances 0.000 description 5
- 229910052759 nickel Inorganic materials 0.000 description 5
- 239000000126 substance Substances 0.000 description 5
- 238000000280 densification Methods 0.000 description 4
- 230000003628 erosive effect Effects 0.000 description 4
- 238000005098 hot rolling Methods 0.000 description 4
- JEIPFZHSYJVQDO-UHFFFAOYSA-N iron(III) oxide Inorganic materials O=[Fe]O[Fe]=O JEIPFZHSYJVQDO-UHFFFAOYSA-N 0.000 description 4
- 238000002844 melting Methods 0.000 description 4
- 230000008018 melting Effects 0.000 description 4
- 239000000203 mixture Substances 0.000 description 4
- UCKMPCXJQFINFW-UHFFFAOYSA-N Sulphide Chemical compound [S-2] UCKMPCXJQFINFW-UHFFFAOYSA-N 0.000 description 3
- 229910001566 austenite Inorganic materials 0.000 description 3
- 230000033228 biological regulation Effects 0.000 description 3
- 229920006395 saturated elastomer Polymers 0.000 description 3
- 238000004088 simulation Methods 0.000 description 3
- 239000003381 stabilizer Substances 0.000 description 3
- QAOWNCQODCNURD-UHFFFAOYSA-N Sulfuric acid Chemical compound OS(O)(=O)=O QAOWNCQODCNURD-UHFFFAOYSA-N 0.000 description 2
- 238000005261 decarburization Methods 0.000 description 2
- 230000007423 decrease Effects 0.000 description 2
- 238000013461 design Methods 0.000 description 2
- 239000012467 final product Substances 0.000 description 2
- ZNNZYHKDIALBAK-UHFFFAOYSA-M potassium thiocyanate Chemical compound [K+].[S-]C#N ZNNZYHKDIALBAK-UHFFFAOYSA-M 0.000 description 2
- 230000001105 regulatory effect Effects 0.000 description 2
- 230000035945 sensitivity Effects 0.000 description 2
- 238000005480 shot peening Methods 0.000 description 2
- 239000000243 solution Substances 0.000 description 2
- 238000005728 strengthening Methods 0.000 description 2
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 2
- YZSCPLGKKMSBMV-UHFFFAOYSA-N 5-fluoro-4-(8-fluoro-4-propan-2-yl-2,3-dihydro-1,4-benzoxazin-6-yl)-N-[5-(1-methylpiperidin-4-yl)pyridin-2-yl]pyrimidin-2-amine Chemical compound FC=1C(=NC(=NC=1)NC1=NC=C(C=C1)C1CCN(CC1)C)C1=CC2=C(OCCN2C(C)C)C(=C1)F YZSCPLGKKMSBMV-UHFFFAOYSA-N 0.000 description 1
- 230000002159 abnormal effect Effects 0.000 description 1
- 229910045601 alloy Inorganic materials 0.000 description 1
- 239000000956 alloy Substances 0.000 description 1
- 239000007864 aqueous solution Substances 0.000 description 1
- 239000011324 bead Substances 0.000 description 1
- 238000005266 casting Methods 0.000 description 1
- 239000003795 chemical substances by application Substances 0.000 description 1
- 230000019771 cognition Effects 0.000 description 1
- 238000009749 continuous casting Methods 0.000 description 1
- 230000001276 controlling effect Effects 0.000 description 1
- 238000005520 cutting process Methods 0.000 description 1
- 230000006378 damage Effects 0.000 description 1
- 230000005518 electrochemistry Effects 0.000 description 1
- 238000005530 etching Methods 0.000 description 1
- 238000002474 experimental method Methods 0.000 description 1
- 239000000284 extract Substances 0.000 description 1
- 239000000446 fuel Substances 0.000 description 1
- 238000012423 maintenance Methods 0.000 description 1
- 239000011159 matrix material Substances 0.000 description 1
- 238000005259 measurement Methods 0.000 description 1
- 229910052750 molybdenum Inorganic materials 0.000 description 1
- 150000004767 nitrides Chemical class 0.000 description 1
- 230000003647 oxidation Effects 0.000 description 1
- 238000007254 oxidation reaction Methods 0.000 description 1
- 230000035515 penetration Effects 0.000 description 1
- 238000012797 qualification Methods 0.000 description 1
- 239000002994 raw material Substances 0.000 description 1
- 238000011160 research Methods 0.000 description 1
- 230000000630 rising effect Effects 0.000 description 1
- 238000005096 rolling process Methods 0.000 description 1
- 238000005204 segregation Methods 0.000 description 1
- 230000035939 shock Effects 0.000 description 1
- 238000007669 thermal treatment Methods 0.000 description 1
- 238000003856 thermoforming Methods 0.000 description 1
- 230000000007 visual effect Effects 0.000 description 1
- 238000010792 warming Methods 0.000 description 1
- 239000002912 waste gas Substances 0.000 description 1
Images
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
-
- 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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/02—Hardening articles or materials formed by forging or rolling, with no further heating beyond that required for the formation
-
- 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
-
- 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
- C22C38/18—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
- C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
-
- 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
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
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- 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
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- Crystallography & Structural Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Manufacturing & Machinery (AREA)
- Heat Treatment Of Articles (AREA)
- Springs (AREA)
- Heat Treatment Of Strip Materials And Filament Materials (AREA)
Abstract
Provided is a spring steel that contains 0.15-0.40% carbon, 1-3.5% silicon, 0.20-2.0% manganese, 0.05-1.20% chromium, at most 0.030% phosphorus, at most 0.02% sulfur, and at least one of the following: 0.005-0.10% titanium, 0.005-0.05% niobium, and at most 0.25% vanadium. The remainder of said spring steel comprises iron and unavoidable impurities. The carbon equivalent (Ceq1) of the provided spring steel, as calculated by formula (1), is at most 0.55. (1) Ceq1 = [C] + 0.108[Si] - 0.067[Mn] + 0.024[Cr] - 0.05[Ni] + 0.074[V] (In formula (1), each symbol in brackets represents the content (mass%) of the corresponding element.).
Description
Technical field
The present invention relates to as the useful spring steel of the former material of wind spring (spring steel), at length saying so relates to the spring steel that when making wind spring, uses, and is that tensile strength is the spring steel of 1900MPa level under the state that quenches.
Background technology
In employed springs (bearing spring etc.) such as automobile, require lightweight in order to reduce waste gas with improving fuel efficiency, point to high strength as an one of which link.The spring of high strength, imperfection sensitivity increases, and for example, produces fracture from the corrosion pit that takes place because of adhering to of Snow Agent easily, and the initial stage that corrosion fatigue causes is lost becomes problem.Therefore just require the also excellent spring of HS and corrosion fatigue characteristic.For example, " UHS1900 " that the applicant developed as spring steel in the past is after being wound into the spring shape, to carry out Q-tempering, can either make tensile strength reach the HS of 1900MPa level, can reach good corrosion fatigue characteristic again.Therefore the wind spring that is obtained by this spring steel is existed side by side HS and good corrosion fatigue characteristic.
Such wind spring generally is through drawing spring steel (wire rod) and carry out the frotton post-heating, hot reel down laggard row quenching, tempering, and the processing (setting) of adjusting is made.Hot rolling around after quenching, temper, be to carry out for the intensity of adjusting spring.When Q-tempering is handled such thermal treatment, a large amount of CO
2Be discharged from.In recent years, be purpose with the load that reduces for global environment, as preventing one of Global warming countermeasure, CO is cut down in strong request
2For this reason, in the manufacturing process of wind spring, also require to reduce CO
2Quantity discharged.
Also have, proposition is in patent documentation 1, does not carry out under the tempered water quenching state carrying out water quenching immediately after the thermoforming, has improved the stabilizer of normal temperature toughness and low-temperature flexibility and has used steel.This stabilizer has with steel and is characterised in that, one-tenth is grouped into is adjusted into the high Mn-Cr of low C-system, or in the high Mn-B-Cr of low C-system, add one or more of Ti, V, Nb.In this patent documentation 1 as the stabilizer of object; Different with the technical field of wind spring; For example, strength level is in the unchallenged 800MPa level of corrosion fatigue characteristic, and the spring in the HS territory (for example 1900MPa level) of existing side by side with desired strength and corrosion fatigue characteristic does not have related.
In addition, the intensity of general iron steel is along with the rising of hardness increases together, if hardness rises, then toughness reduces in addition.Promptly; If the intensity increase of iron steel then toughness reduces; But as the spring material; Then requiring has spring can tolerate the destruction characteristic of harsh environment for use; Even in the spring of bearing spring of high strength etc.; Still need guarantee its toughness, particularly important low-temperature flexibility in the use of cold district.
For example, patent documentation 2 is open, and through regulating various compositions, in high-strength spring steel, its ductility and toughness improve, and patent documentation 3 discloses in addition, has hardness and flexible spring steel concurrently through regulating various compositions, can accessing.But patent documentation 2 and 3 all just is conceived to the toughness under the normal temperature, does not give consideration for low-temperature flexibility.Toughness under the low temperature is usually than the poor toughness under the normal temperature, if consider from patent documentation 2 and 3 disclosed normal temperature toughness, then the low-temperature flexibility in patent documentation 2 and 3 the technology is insufficient.
The look-ahead technique document
Patent documentation
Patent documentation 1: No. 4406341 communique of patent
Patent documentation 2: No. 3577411 communique of patent
Patent documentation 3: No. 3246733 communique of patent
Summary of the invention
The present invention is conceived to above-mentioned such situation and does, and its purpose is, a kind of spring steel is provided; It is when being processed into wind spring; Even omit the temper after quenching, HS and good corrosion fatigue characteristic are existed side by side, can make the also excellent wind spring of low-temperature flexibility in addition.In addition, another object of the present invention is to, the spring that is obtained by this spring steel is provided.
The high-strength spring of the present invention that can solve above-mentioned problem is used steel, contains the C:0.15～0.40% (meaning of quality %.Down together.), Si:1～3.5%, Mn:0.20～2.0%; And contain at least a kind of from Ti:0.005～0.10%, Nb:0.005～0.05% and the crowd that constitutes below the V:0.25%, selecting, Cr:0.05～1.20%, below the P:0.030%, below the S:0.02%; Surplus is iron and unavoidable impurities, by the carbon equivalent Ceq shown in the following formula (1)
1Be below 0.55.
Ceq
1＝[C]+0.108×[Si]-0.067×[Mn]+0.024×[Cr]-0.05×[Ni]+0.074×[V]…(1)
(in the following formula (1), [] represented the content (quality %) of each element.)
Spring steel of the present invention also can contain following element: (a) below Ni:0.05～2% and Cu:0.05～0.50%, (b) Ni:0.15～2% and Cu:0.05～0.50%, (c) B:0.005% and/or below the Mo:0.60% as required.
In addition, spring steel of the present invention also preferably contains at least a kind that from the crowd that Ti:0.035～0.10%, Nb:0.005～0.05% and V:0.05～0.25% constitutes, selects, and the grain size number after the quenching is more than 7.5 degree.
If use above-mentioned spring steel, this spring steel is reeled down hot, after quenching,, then can produce the spring that above-mentioned characteristic is existed side by side to omit the processing of directly adjusting of tempered state.
Spring steel of the present invention; Because suitably controlled the amount of element and allotment balance of specific alloying element; So when using this spring steel to make wind spring; Can omit the temper after the quenching, under this state of quenching, HS and good corrosion fatigue characteristic are existed side by side, can make spring in addition with good low-temperature flexibility.
Description of drawings
Fig. 1 is the carbon equivalent (Ceq of the test film that obtains among the embodiment 1 of expression
1) with the graph of hydrogen embrittlement crackle life relation.
Fig. 2 is the tensile strength and the low-temperature flexibility (vE of the test film that obtains among the embodiment 2 of expression
-50) concern graph.
Embodiment
When present inventors make spring at wind spring with steel; In order to be omitted in the temper after the quenching of carrying out behind the coiling and HS and good corrosion fatigue characteristic are existed side by side; Can to make the also spring steel of excellent spring of low-temperature flexibility in order providing in addition, to have carried out research with keen determination repeatedly.Its result finds, if make the kind of the basic alloys element that spring steel contains narrow down to C, Si, Mn, Cr, and Ti, Nb and V at least a kind; Or be retracted in these groups of elements and add (i) Ni and Cu again, or (ii) B and/or Mo, and; Among these elements, the amount of C, Ti, Nb, V, Cr, Ni and Cu reduces as far as possible, on the other hand; Contain Si and Mn energetically, when then making spring, can omit the temper after the quenching reeling this spring steel; Under such state that quenches, the tensile strength of 1900MPa level and good corrosion fatigue characteristic are existed side by side, in addition through adjust the content of Ti, Nb and V tightlyer; Can provide low-temperature flexibility also excellent spring, thereby accomplish the present invention.
In spring steel of the present invention, have especially and be characterised in that, the C amount is reduced than the employed C amount of common spring steel.Through reducing the C amount, can be reduced in the carbide amount of separating out in the steel, so can be omitted in the tempering after the quenching of carrying out in the common spring manufacturing processed.That is, it makes spring as above-mentioned, normally through heating behind drawing spring steel (wire rod) and the frotton, hot rolling around after quench, tempering, the processing of adjusting again is made.Adjust handle after, carry out bead based on needs after, implement application.But spring steel of the present invention is because reduced the C amount, so even omit tempering and the processing of directly adjusting after quenching, also can guarantee the intensity of spring.
On the other hand, in spring steel of the present invention, add Si and Mn energetically.Si and Mn are the elements that obtains easily, even if Si and Mn amount are increased, still can keep stable supplying property.In addition, because Si and Mn have the effect that toughness is reduced and improve intensity, so, HS and good corrosion fatigue characteristic are existed side by side through adding Si and Mn energetically.
,, need to stipulate the amount of each element tightly, and will stipulate their relation based on above cognition on one side Yi Bian HS and good corrosion fatigue characteristic are existed side by side.That is, in the present invention, the one-tenth that designs spring steel as follows is grouped into, and makes the carbon equivalent Ceq shown in the following formula (1)
1Be below 0.55.In the following formula (1), the content (quality %) of each element in [] expression steel.
< one-tenth of spring steel is grouped into >
Contain C:0.15～0.40%, Si:1～3.5%, Mn:0.20～2.0%, and contain at least a kind, Cr:0.05～1.20% of from Ti:0.005～0.10%, Nb:0.005～0.05% and the crowd that constitutes below the V:0.25%, selecting
Ceq
1＝[C]+0.108×[Si]-0.067×[Mn]+0.024×[Cr]-0.05×[Ni]+0.074×[V]…(1)
The addition of each element is set reason and carbon equivalent Ceq
1Regulation the reasons are as follows.
Why making C is more than 0.15%, is in order to improve hardenability, to guarantee intensity.In addition, why making C below 0.40%, is in order to prevent the deterioration of toughness and corrosion fatigue characteristic.The lower limit of C amount is preferably more than 0.2%, and more preferably more than 0.25%, the upper limit of C amount is preferably below 0.35%, more preferably below 0.34%, is preferably below 0.33% especially.
Why making Si is more than 1%, is in order Si to be played a role as the solution strengthening element, to guarantee intensity.Si is lower than at 1% o'clock, and matrix strength is not enough.On the other hand, superfluous if the Si quantitative change gets, then when quenching heating carbide penetrate insufficiently, need more pyritous heating for austenitizing equably, the fatigue characteristic variation of spring is carried out in the decarburization on surface.Therefore, through making Si below 3.5%, can suppress the generation of aforesaid decarburization and grain boundary oxidation etc., can prevent that abnormal structure from generating, intensity reduces.Si is preferably more than 1.5%, below 3.0%, more preferably more than 1.80%, below 2.5%.
Mn is more than 0.20%, can improve hardenability, can intensity.Sulfide-based in addition inclusion generates, and can suppress the embrittlement of grain boundaries that causes because of S, makes the raising of toughness and corrosion fatigue characteristic.In addition, Mn is below 2.0%, crosses cold tissue and takes place, and can prevent toughness and corrosion fatigue deterioration in characteristics.In addition, the generation and thickization of the sulfide-based inclusion of surplus be can suppress, toughness and corrosion fatigue deterioration in characteristics prevented.The lower limit of Mn amount is preferably more than 0.5%, and more preferably more than 0.80%, the upper limit of Mn amount is preferably below 1.8%, is preferably below 1.5% especially.
Why making Ti is more than 0.005%, is in order to make the old austenite crystal miniaturization after the quenching, to improve intensity and yield strength ratio, improving toughness and corrosion fatigue characteristic.Through toughness is improved, can improve elasticity attenuation resistance (sag resistance).In addition, why making Ti below 0.10%, is in order to prevent that thick inclusion (for example Ti nitride) from separating out, to suppress the deterioration of corrosion fatigue characteristic.The lower limit of Ti amount is preferably more than 0.01% and (is preferably more than 0.05% especially), and the upper limit of Ti amount is preferably below 0.080%, more preferably below 0.07%.
V further improves hardenability, is to improving the element that intensity effectively plays a role.It improves toughness and helps the raising of elasticity attenuation resistance in addition, and it makes the crystal grain miniaturization in addition, is the element that makes intensity and yield strength ratio raising.In order to bring into play such effect, V preferably makes it to contain more than 0.05%, more preferably more than 0.08%, further is preferably more than 0.1%.But, then form thick carbonitride, toughness and corrosion fatigue deterioration in characteristics if V is superfluous.Therefore V is below 0.25%, is preferably below 0.22%, more preferably below 0.2%.
Nb improves toughness, is the element that helps the raising of elasticity attenuation resistance, and it makes the crystal grain miniaturization in addition, is the element that intensity and yield strength ratio are improved.In order to bring into play such effect, the Nb amount is more than 0.005%.The Nb amount is preferably more than 0.008%, more preferably more than 0.01%.On the other hand, if the Nb amount is superfluous, then bring the toughness detrimentally affect.Therefore the Nb amount is below 0.05%.The Nb amount is preferably below 0.04%, more preferably below 0.03%.
Ti, V and Nb can add separately, also can make up two or more interpolations.The content of Ti, V and Nb is respectively, and Ti:0.035～0.10%, Nb:0.005～0.05%, V:0.05～0.25% preferably contain its at least a kind.In addition,, contacts ground performance crystal grain micronized effect can be arranged, can make grain size number after the quenching, consequently can bring into play good low-temperature flexibility more than No. 7.5 through containing Ti, V and Nb in such scope.Grain size number after the quenching more preferably more than No. 8.0, further is preferably more than No. 9.0.The low-temperature flexibility of spring steel of the present invention, the impact absorbing energy under for example-50 ℃ is 50J/cm
2More than, be preferably 70J/cm
2More than, 80J/cm more preferably
2More than.
Cr is more than 0.05%, through solution strengthening its body of steel is strengthened, and hardenability is improved, and can guarantee intensity.In addition, making the rust that is created on skin section under the etching condition is amorphousness and densification, is the element that helps the raising of erosion resistance.On the other hand, Cr is below 1.20%, and the Ms point reduces, and can prevent that cold tissue from generating, and guarantees toughness and corrosion fatigue characteristic, in addition, and the intensity that causes because of the low penetration of Cr carbide in the time of can preventing to quench and the minimizing of hardness.Cr is preferably more than 0.1%, below 1.10%, more preferably more than 0.5%, below 1.05%.
The surplus of spring steel of the present invention comes down to iron.But the unavoidable impurities that allows certainly to sneak into because of the situation of goods and materials, manufacturing equipments etc. such as iron material (comprising scrap iron) and auxiliary material is included in the steel.Among the unavoidable impurities, special stipulation P is below 0.030%, and S is below 0.02%.Stipulate the reasons are as follows of this scope.
Why making P below 0.030%, is to make embrittlement of grain boundaries in old austenite grain boundary segregation altogether in order to suppress, and prevents toughness and corrosion fatigue deterioration in characteristics.P is preferably below 0.02%, more preferably below 0.01%.The degree that P is few more is preferred more, but contains about 0.001% usually.
Why making S below 0.02%, is in order to prevent that it from forming sulfide-based inclusion in steel, this thickization of inclusion and cause the corrosion fatigue characteristic to reduce.S is preferably below 0.015%, is preferably below 0.01% especially.The same few more degree with P of S is preferred more, but contains about 0.001% usually.
The total amount of P and S is preferably below 0.015%, more preferably below 0.010%.
Why make above-mentioned carbon equivalent Ceq
1Being below 0.55, is for when wind spring is made wind spring with steel, even omit the temper after quenching, the intensity of spring and corrosion fatigue characteristic is existed side by side.That is above-mentioned carbon equivalent Ceq,
1The contribution degree of the alloying element that expression impacts the hardness after quenching after reducing this numerical value, through omitting the temper after quenching, can be guaranteed the core hardness of spring, can reach high strength.In addition, with above-mentioned carbon equivalent Ceq
1Be suppressed at below 0.55, can reduce the interdependency of alloying element, can improve stable supplying property.Above-mentioned carbon equivalent Ceq
1Be preferably below 0.53, more preferably below 0.50.Also have, though above-mentioned carbon equivalent Ceq
1Can cutting down cost to make it method that little mode is carried out to branch design as far as possible, but, still need add alloying element to a certain extent for HS and corrosion fatigue characteristic are existed side by side.So carbon equivalent Ceq
1Lower value be 0.30.Also have, when calculating following formula (1), when having the element that is not contained, the content of this element calculates as 0 quality %.
Spring steel of the present invention satisfies above-mentioned chemical ingredients and forms and above-mentioned carbon equivalent Ceq
1, but to pursue the further improvement of characteristic, also Ni and Cu be can contain, or B and/or Mo contained.
When containing Ni and Cu (promptly and with Ni and Cu), making the Ni amount is 0.05～2%, and the Cu amount is 0.05～0.50%.Why making Ni is more than 0.05%, is in order to improve toughness, to reduce imperfection sensitivity, the corrosion fatigue characteristic being improved.In addition, it is amorphousness and densification that Ni makes the rust of generation, has the effect that improves erosion resistance, has the effect of improvement as the important permanent residual strain characteristic of spring characteristic in addition.On the other hand, through making Ni below 2%, the Ms point reduces, and can prevent that cold tissue from generating, and guarantees toughness and corrosion fatigue characteristic.Ni is preferably more than 0.15%, below 2%, more preferably more than 0.18%, below 1.5%, further be preferably more than 0.20%, below 1%, particularly preferably in below 0.5%.
Cu than iron expensive (Noble) element, therefore makes the rust densification on electrochemistry, be to have the element that the erosion resistance of making improves this effect.When therefore containing Cu, making the Cu amount is more than 0.05%.Even but superfluous the interpolation, its effect also is saturated, might cause the raw-material embrittlement in heat is pricked on the contrary.Therefore the Cu amount on be limited to below 0.50%.Cu is preferably more than 0.1%, below 0.4%, more preferably (is preferably more than 0.18% especially) more than 0.15%, below 0.3%.
B further improves hardenability, improves grain-boundary strength, improves toughness and elasticity attenuation resistance is improved, and makes the rust densification that is created on the surface in addition, is the element that erosion resistance is improved.In order to bring into play such effect, B preferably contains more than 0.0005%, more preferably more than 0.001%, further is preferably more than 0.0015%.But superfluous if B becomes, then except above-mentioned effect is saturated, also can form thick carbonitride, toughness and corrosion fatigue deterioration in characteristics.Therefore B is preferably below 0.004%, more preferably below 0.003% below 0.005%.
Mo improves toughness, is the element that helps elasticity attenuation resistance to improve, and guarantees hardenability in addition, is intensity and the flexible element that improves steel.In order to bring into play such effect effectively, the Mo amount is preferably more than 0.05%, more preferably more than 0.08%, further is preferably more than 0.10%.On the other hand, even the Mo amount is superfluous, above-mentioned effect also is saturated.Therefore the Mo amount is preferably below 0.60%, more preferably below 0.50%, further is preferably below 0.35%.B and Mo can contain separately, also can and use.
As above explain; Spring steel of the present invention is characterized in that; Tightly stipulate each alloying element amount, and stipulate their relation, if use this spring steel; Then can be omitted in the temper after the quenching of carrying out behind the coiling, can be manufactured on tensile strength under the as-quenched condition and still reach the spring that the above HS of 1900MPa and good corrosion fatigue characteristic are existed side by side.In addition, the content of the element (Ti, Nb and V) through controlling crystal grain miniaturization effect tightlyer can make low-temperature flexibility improve.Below, the method when making spring by above-mentioned spring steel describes.
When making spring, need to omit the tempering after quenching by spring steel of the present invention.That is, carry out drawing, frotton post-heating for the spring steel (wire rod) that satisfies above-mentioned chemical ingredients composition, forming shape at hot coiling down is the spring shape, all identical with in the past up to quenching, but after quenching, need omit tempering and the processing of directly adjusting.Spring steel of the present invention is because the C amount decreases than existing spring steel, so if after quenching, carry out tempering, then overbate toughness and corrosion fatigue deterioration in characteristics.Therefore need to omit the tempering after quenching.
At this, so-called " tempered omission ", the meaning is after quenching, is not heated to surpass 350 ℃ temperature.
Above-mentioned adjusting handled and can under cold conditions, be carried out, and also can under warm attitude, carry out.The temperature that cold conditions is adjusted when handling is that normal temperature gets final product, and the temperature that warm attitude is adjusted when handling is to get final product about 200～250 ℃.
Adjust after the processing, also can carry out shot peening as required, carry out application afterwards again.The condition of shot peening and application is not special to be limited, and can adopt the condition of ordinary method.
The spring that so obtains can make HS and good corrosion fatigue characteristic exist side by side, and low-temperature flexibility is also excellent in addition.
Not special qualification of creating conditions of spring steel of the present invention, but, that is, grain size number is reached more than No. 7.5 in order to reach the preferred form of the present invention, the Heating temperature when for example recommending to quench is below 925 ℃, and heat-up time is below 15 minutes.Heating temperature during aforementioned quenching the and the lower limit of heat-up time are not special to be limited, but the following of Heating temperature is limited to about 850 ℃ usually, and the lower limit of heat-up time is about 10 minutes.
[embodiment]
Below, enumerate embodiment the present invention more specifically is described, but the present invention is not limited by following embodiment certainly, can certainly suitably change enforcement in the scope of the aim of before and after can meeting, stating, these all are included in the scope of technology of the present invention.
Embodiment 1
The steel of forming with the chemical ingredients shown in the vacuum melting furnace melting below table 1 of 150kg (surplus is iron and unavoidable impurities) afterwards; With 1200 ℃ of maintenances; Carry out forge hot afterwards; Become the billet of length of side 155mm size, this billet is carried out hot rolling and makes the spring steel (spring wire rod) of diameter 13.5mm.Implement frotton processing for this spring wire rod, make its diameter become 12.5mm after, cut into length 70mm, quench thereafter.Quenching, it is after 10 minutes, to put into the oil groove of 50 ℃ of temperature with 925 ℃ of heating of temperature again.Carry out mechanical workout after the quenching, cut into the test film of wide 10mm * thick 1.5mm * long 65mm.
No.29 shown in the table 1 and No.30 have simulated Kobe Steel, Ltd (KOBE STEEL; LTD) data of the spring wire rod " UHS1900 " of system; Wherein, No.30 is after quenching, keeps 1 hour and carried out carrying out mechanical workout and being made into test film with condition same as described above after the tempering with 400 ℃.Show in the table 2 and have or not tempering.
In addition, chemical ingredients amount in the steel and the carbon equivalent (Ceq that calculates according to following formula (1)
1) result is presented in the below table 1.
Investigate for the intensity and the corrosion fatigue characteristic of resulting test film as follows.
The intensity of test film and corrosion fatigue characteristic, simulation are adjusted to handle under cold conditions or warm attitude and are measured.That is, the simulation cold conditions is adjusted when handling, and above-mentioned test film directly is used for each test, and the simulation temperature attitude is adjusted when handling, and above-mentioned test film with 200 ℃ of heating 60 minutes, is used for each test.No matter simulate cold conditions and adjust and handle which kind of processing of adjusting and handling, all show in the below table 2 with warm attitude.
< intensity >
The intensity of test film is to use Rockwell hardness tester, estimates with the hardness of C calibration experiment with measuring sheet.The The measured results show of C hardness is in below table 2.In the present invention, HRC is being qualified more than 51.
< corrosion fatigue characteristic >
The corrosion fatigue characteristic is carried out the hydrogen embrittlement crack test and is estimated.The hydrogen embrittlement crack test; Be for above-mentioned test film; Through 4 crooked one side the stress of 1400MPa is worked; On one side this test film is immersed in the mixed aqueous solution of sulfuric acid (0.5Mol/L) and Rhocya (KSCN:0.01Mol/L), use potentiostat apply than SCE electrode low (Lower)-voltage of 700mV, measure time up to the crackle generation (below be called the hydrogen embrittlement crackle life-span.)。The The measured results show of hydrogen embrittlement crack test is in below table 2.In the present invention, the time to the crackle generation is qualified in time more than 600 seconds.
Also have, HRC is more than 51, and the time of taking place to crackle is that this standard means more than 600 seconds, has and is carrying out the characteristic of the resulting existing bearing spring of tempering (No.30 of below table 2) more than equal after the quenching.
Show carbon equivalent (Ceq among Fig. 1
1) with the relation in hydrogen embrittlement crackle life-span (second).In Fig. 1, No.1～15,31,33 result represent by, No.16～29,32 result by ● expression, the result of No.30 (tempering is arranged) is by zero expression.
Can know following tendency by Fig. 1, reduce carbon equivalent (Ceq
1) method, can prolong the hydrogen embrittlement crackle life-span, can improve the corrosion fatigue characteristic.
Can investigate as follows by table 2.
No.30 carries out the tempered example after quenching.In this example, can guarantee core hardness, intensity is high, in addition the hydrogen embrittlement crackle life-span also good, can improve the corrosion fatigue characteristic.But because after quenching, carry out temper, so can not cut down CO
2Quantity discharged.
The one-tenth of No.29 is grouped into above-mentioned No.30 similar, but after quenching, omits the tempered example.In this example, because omit temper, so can cut down CO
2Quantity discharged, carbon equivalent surpasses 0.55, although the alloying element amount is many, but because omit tempering, so core hardness is really up to the mark, toughness reduces, the hydrogen embrittlement crackle life-span is short, the corrosion fatigue deterioration in characteristics.
No.16～28, the 32nd, the example of the important document of regulation can not make HS and good corrosion fatigue characteristic exist side by side in the discontented unabridged version invention.That is carbon equivalent (the Ceq of spring steel,
1) surpass the scope of the present invention's regulation, and omitted the tempering after quenching, therefore, though can subdue CO
2Quantity discharged, but core hardness is really up to the mark, toughness reduces, and the hydrogen embrittlement crackle life-span is short, the corrosion fatigue deterioration in characteristics.
The example of the important document of the present invention regulation is satisfied in No.1～15, the 33rd, and HS and good corrosion fatigue characteristic are existed side by side.That is, through with carbon equivalent (Ceq
1) be suppressed at below 0.55, because omitted the tempering after quenching, so can cut down CO
2Quantity discharged, and can appropriateness guarantee core hardness, can reach HS.In addition, the hydrogen embrittlement crackle life-span is also long, also can improve the corrosion fatigue characteristic.And, because with the carbon equivalent (Ceq of spring steel
1) be suppressed at below 0.55, so can reduce the interdependency of alloying element, realize stable supplying.Therefore can know,, the above-mentioned No.30 that given play to and simulated above-mentioned " UHS1900 " can be provided then the spring with degree or higher characteristic if use spring steel of the present invention.
[table 1]
[table 2]
Embodiment 2
Behind the steel (surplus is iron and unavoidable impurities) with the composition of the chemical ingredients shown in the vacuum melting furnace melting table 3 of 150kg; Cast through ingot casting method or Continuous casting process; Thereafter; Be made into the big or small billet of length of side 155mm through split rolling method, carry out hot rolling again, the wire rod that is processed into diameter 13.5mm is as supplying the examination material.Supply the examination material after 10 minutes with 925 ℃ temperature heating, the oil groove of putting into 50 ℃ quenches.Has only No.2-24 after aforementioned quenching, with 400 ℃ of temper of carrying out 1 hour.
[table 3]
< low-temperature flexibility >
Confession examination material after above-mentioned quenching extracts the shock test sheet that 2mm is with the U otch, tries to achieve the impact absorbing energy (vE under-50 ℃ according to JISZ2242
-50).Test is respectively carried out 2 for each steel grade, with the impact absorbing energy of MV as each steel grade.
< grain size number number >
The D/4 position (D is the diameter of wire rod) of confession after above-mentioned quenching examination material is with observation by light microscope 15mm arbitrarily
2Zone (multiplying power: 400 times), measure grain size number number according to JIS G0551.Measurement is carried out in 2 visuals field, with its MV as the austenite crystal granularity.
The result is presented in the table 4.
[table 4]
No.2-1～the No.2-14 of table 4 satisfies important document of the present invention, particularly Ti, Nb and V amount and is suitably adjusted, and therefore can realize the steel that HS and low-temperature flexibility are also excellent.
On the other hand, No.2-15～No.2-24 is some at least because of the important document of being discontented with the unabridged version invention, so toughness is insufficient.
No.2-15～No.2-19 is the superfluous example of C amount, because intensity excessively rises, causes low-temperature flexibility to reduce.
No.2-20～No.2-22 is not because Ti, Nb and V any one is contained, so can't bring into play the crystal grain micronized effect, low-temperature flexibility reduces.
No.2-23 and No.2-24 all are 9254 the steel grades that are equivalent to gauge steel, and No.2-24 carries out temper after quenching.Its C amount of No.2-23 is many, and intensity excessively rises, and any one of Ti, Nb and V all do not contain, so low-temperature flexibility reduces.In addition, No.2-24 has been because carried out temper, thus strength ratio No.2-23 decrease, but because any one of Ti, Nb and V all do not contain, so low-temperature flexibility reduces.
Fig. 2 is illustrated among No.2-1～2-24, intensity and low-temperature flexibility (50 ℃ and impact absorbing energy) concern graph.Among Fig. 2, the result of No.2-1～2-14,2-25 representes by, the result of No.2-15～No.2-23,2-26 by ● expression, the result of No.2-24 is by zero expression.Can know that according to Fig. 2 satisfy the steel (being represented by among Fig. 2) of important document of the present invention, impact absorbing energy is all at 50J/cm
2More than, and with the steel of a certain important document of discontented unabridged version invention (among Fig. 2 by ● represent with zero) compare, can reach H.T. when under equality strength, comparing.
Claims (6)
1. an omission tempered high-strength spring is used steel; It is characterized in that; Contain C:0.15～0.40%, Si:1～3.5%, Mn:0.20～2.0% in quality %; And contain from by at least a kind of element selecting Ti:0.005～0.10%, Nb:0.005～0.05% and the crowd that constitutes below the V:0.25% and Cr:0.05～1.20%, below the P:0.030%, below the S:0.02%, surplus is iron and unavoidable impurities
By the carbon equivalent Ceq shown in the following formula (1)
1Be below 0.55,
Ceq
1＝[C]+0.108×[Si]-0.067×[Mn]+0.024×[Cr]-0.05×[Ni]+0.074×[V]…(1)
In the following formula (1), [] represented the mass percentage content of each element.
2. high-strength spring according to claim 1 is used steel, wherein, contains Ni:0.05～2% and Cu:0.05～0.50% in quality %.
3. high-strength spring according to claim 2 is used steel, wherein, contains Ni:0.15～2% in quality %.
4. high-strength spring according to claim 1 is used steel; Wherein, Contain at least a kind of element from the crowd who is made up of Ti:0.035～0.10%, Nb:0.005～0.05% and V:0.05～0.25%, selecting in quality %, the grain size number after the quenching is more than No. 7.5.
5. high-strength spring according to claim 1 is used steel, wherein, also contains below the B:0.005% and/or below the Mo:0.60% in quality %.
6. the method for manufacture of the high-strength spring of a corrosion fatigue excellent is characterized in that, each described spring steel in the coiling claim 1～5 under hot state is after quenching, to omit the processing of adjusting of tempered state.
Applications Claiming Priority (3)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2009291143 | 2009-12-22 | ||
| JP2009-291143 | 2009-12-22 | ||
| PCT/JP2010/073003 WO2011078165A1 (en) | 2009-12-22 | 2010-12-21 | High-strength spring steel |
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| Publication Number | Publication Date |
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| CN102482743A true CN102482743A (en) | 2012-05-30 |
| CN102482743B CN102482743B (en) | 2014-12-24 |
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| US (2) | US20120285585A1 (en) |
| EP (1) | EP2518175B1 (en) |
| JP (2) | JP6027302B2 (en) |
| KR (1) | KR20120084810A (en) |
| CN (1) | CN102482743B (en) |
| BR (1) | BR112012014178A2 (en) |
| ES (1) | ES2709515T3 (en) |
| WO (1) | WO2011078165A1 (en) |
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| CN105112774A (en) * | 2015-08-28 | 2015-12-02 | 浙江美力科技股份有限公司 | Air cooling hardened spring steel with high obdurability, low-medium-carbon and microalloy and forming and heat treatment process thereof |
| CN106011634A (en) * | 2016-07-26 | 2016-10-12 | 路望培 | Spring mechanical material and preparation method thereof |
| CN106636896A (en) * | 2016-12-05 | 2017-05-10 | 武汉钢铁股份有限公司 | High hardenability hot-rolled knife board steel |
| CN107354388A (en) * | 2017-07-25 | 2017-11-17 | 西华大学 | A kind of high-strength and high ductility bainite spring steel and its manufacture method |
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| JP6033796B2 (en) * | 2012-01-31 | 2016-11-30 | 日本発條株式会社 | Ring-shaped spring and method for manufacturing the same |
| JP2014198874A (en) | 2013-03-29 | 2014-10-23 | 株式会社神戸製鋼所 | Steel material excellent in corrosion resistance and magnetic properties and method of producing the same |
| JP6477007B2 (en) * | 2015-02-26 | 2019-03-06 | 愛知製鋼株式会社 | Leaf spring and manufacturing method thereof |
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| KR101795278B1 (en) * | 2016-06-21 | 2017-11-08 | 현대자동차주식회사 | Ultra high strength spring steel |
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| JP2001049337A (en) * | 1999-08-05 | 2001-02-20 | Kobe Steel Ltd | Production of high strength spring excellent in fatigue strength |
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2010
- 2010-10-26 JP JP2010240097A patent/JP6027302B2/en active Active
- 2010-12-21 KR KR1020127016111A patent/KR20120084810A/en not_active Ceased
- 2010-12-21 BR BR112012014178A patent/BR112012014178A2/en not_active Application Discontinuation
- 2010-12-21 CN CN201080039360.2A patent/CN102482743B/en active Active
- 2010-12-21 ES ES10839395T patent/ES2709515T3/en active Active
- 2010-12-21 WO PCT/JP2010/073003 patent/WO2011078165A1/en active Application Filing
- 2010-12-21 EP EP10839395.0A patent/EP2518175B1/en active Active
- 2010-12-21 US US13/511,541 patent/US20120285585A1/en not_active Abandoned
-
2015
- 2015-06-30 JP JP2015131070A patent/JP2015214754A/en active Pending
-
2016
- 2016-10-05 US US15/286,065 patent/US20170022580A1/en not_active Abandoned
Patent Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2001049337A (en) * | 1999-08-05 | 2001-02-20 | Kobe Steel Ltd | Production of high strength spring excellent in fatigue strength |
Cited By (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN105088081A (en) * | 2015-08-28 | 2015-11-25 | 浙江美力汽车弹簧有限公司 | Bainite and martensite spring steel for stabilizer bar and manufacturing process for stabilizer bar |
| CN105112774A (en) * | 2015-08-28 | 2015-12-02 | 浙江美力科技股份有限公司 | Air cooling hardened spring steel with high obdurability, low-medium-carbon and microalloy and forming and heat treatment process thereof |
| CN105112774B (en) * | 2015-08-28 | 2017-12-01 | 浙江美力科技股份有限公司 | The air-cooled hardening spring steel of the low middle carbon microalloy of high-strength tenacity and its shaping and Technology for Heating Processing |
| CN106011634A (en) * | 2016-07-26 | 2016-10-12 | 路望培 | Spring mechanical material and preparation method thereof |
| CN106636896A (en) * | 2016-12-05 | 2017-05-10 | 武汉钢铁股份有限公司 | High hardenability hot-rolled knife board steel |
| CN107354388A (en) * | 2017-07-25 | 2017-11-17 | 西华大学 | A kind of high-strength and high ductility bainite spring steel and its manufacture method |
| CN107354388B (en) * | 2017-07-25 | 2019-03-01 | 西华大学 | A kind of high-strength and high ductility bainite spring steel and its manufacturing method |
| CN114134411A (en) * | 2021-10-12 | 2022-03-04 | 江阴兴澄特种钢铁有限公司 | Spheroidized annealed steel for low-temperature-resistant high-strength ball screw and manufacturing method thereof |
Also Published As
| Publication number | Publication date |
|---|---|
| JP6027302B2 (en) | 2016-11-16 |
| EP2518175B1 (en) | 2019-01-23 |
| US20120285585A1 (en) | 2012-11-15 |
| EP2518175A1 (en) | 2012-10-31 |
| JP2015214754A (en) | 2015-12-03 |
| EP2518175A4 (en) | 2015-12-02 |
| WO2011078165A1 (en) | 2011-06-30 |
| KR20120084810A (en) | 2012-07-30 |
| CN102482743B (en) | 2014-12-24 |
| ES2709515T3 (en) | 2019-04-16 |
| BR112012014178A2 (en) | 2016-07-05 |
| US20170022580A1 (en) | 2017-01-26 |
| JP2011149089A (en) | 2011-08-04 |
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