CN104313483A - High-carbon cold-rolled automobile diaphragm spring steel and production method thereof - Google Patents
High-carbon cold-rolled automobile diaphragm spring steel and production method thereof Download PDFInfo
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- 229910000639 Spring steel Inorganic materials 0.000 title claims abstract description 21
- 229910052799 carbon Inorganic materials 0.000 title claims abstract description 19
- 238000004519 manufacturing process Methods 0.000 title abstract description 15
- 238000005496 tempering Methods 0.000 claims abstract description 18
- 238000010791 quenching Methods 0.000 claims abstract description 17
- 238000005097 cold rolling Methods 0.000 claims abstract description 16
- 238000000137 annealing Methods 0.000 claims abstract description 14
- 230000000171 quenching effect Effects 0.000 claims abstract description 14
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims abstract description 13
- 238000010438 heat treatment Methods 0.000 claims abstract description 12
- 238000005520 cutting process Methods 0.000 claims abstract description 10
- 238000012545 processing Methods 0.000 claims abstract description 10
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 9
- 238000010583 slow cooling Methods 0.000 claims abstract description 9
- 229910052698 phosphorus Inorganic materials 0.000 claims abstract description 8
- 229910052717 sulfur Inorganic materials 0.000 claims abstract description 8
- 238000009749 continuous casting Methods 0.000 claims abstract description 6
- 238000007689 inspection Methods 0.000 claims abstract description 6
- 238000003723 Smelting Methods 0.000 claims abstract description 5
- 238000005098 hot rolling Methods 0.000 claims abstract description 5
- 229910052742 iron Inorganic materials 0.000 claims abstract description 4
- 238000007670 refining Methods 0.000 claims abstract description 4
- 229910052757 nitrogen Inorganic materials 0.000 claims abstract description 3
- 238000000034 method Methods 0.000 claims description 14
- 238000005096 rolling process Methods 0.000 claims description 13
- 229910052720 vanadium Inorganic materials 0.000 claims description 10
- 229910052804 chromium Inorganic materials 0.000 claims description 9
- 229910052759 nickel Inorganic materials 0.000 claims description 8
- 229910000734 martensite Inorganic materials 0.000 claims description 7
- 238000002791 soaking Methods 0.000 claims description 6
- 229910052710 silicon Inorganic materials 0.000 claims description 5
- 238000001816 cooling Methods 0.000 claims description 4
- 230000006698 induction Effects 0.000 claims description 4
- 238000003756 stirring Methods 0.000 claims description 4
- 238000005266 casting Methods 0.000 claims description 3
- 230000003009 desulfurizing effect Effects 0.000 claims description 3
- 238000009413 insulation Methods 0.000 claims description 3
- 230000011218 segmentation Effects 0.000 claims description 3
- 229910000831 Steel Inorganic materials 0.000 abstract description 59
- 239000010959 steel Substances 0.000 abstract description 59
- 238000009847 ladle furnace Methods 0.000 abstract 2
- 230000000712 assembly Effects 0.000 abstract 1
- 238000000429 assembly Methods 0.000 abstract 1
- 239000000470 constituent Substances 0.000 abstract 1
- 239000011651 chromium Substances 0.000 description 12
- 239000000203 mixture Substances 0.000 description 7
- 238000013461 design Methods 0.000 description 6
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 5
- 230000000052 comparative effect Effects 0.000 description 5
- 239000012535 impurity Substances 0.000 description 5
- 238000005204 segregation Methods 0.000 description 5
- 230000002929 anti-fatigue Effects 0.000 description 4
- 239000000126 substance Substances 0.000 description 4
- 238000007669 thermal treatment Methods 0.000 description 4
- 229910001566 austenite Inorganic materials 0.000 description 3
- 239000013078 crystal Substances 0.000 description 3
- 230000007423 decrease Effects 0.000 description 3
- 230000000694 effects Effects 0.000 description 3
- 239000007789 gas Substances 0.000 description 3
- 238000005554 pickling Methods 0.000 description 3
- 238000010008 shearing Methods 0.000 description 3
- 238000005275 alloying Methods 0.000 description 2
- 230000015572 biosynthetic process Effects 0.000 description 2
- 229910001567 cementite Inorganic materials 0.000 description 2
- 230000007812 deficiency Effects 0.000 description 2
- KSOKAHYVTMZFBJ-UHFFFAOYSA-N iron;methane Chemical compound C.[Fe].[Fe].[Fe] KSOKAHYVTMZFBJ-UHFFFAOYSA-N 0.000 description 2
- 238000003801 milling Methods 0.000 description 2
- 238000009628 steelmaking Methods 0.000 description 2
- 230000003245 working effect Effects 0.000 description 2
- 229910000851 Alloy steel Inorganic materials 0.000 description 1
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 description 1
- 238000003556 assay Methods 0.000 description 1
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 1
- 239000010960 cold rolled steel Substances 0.000 description 1
- 238000005261 decarburization Methods 0.000 description 1
- 238000009826 distribution Methods 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 229910052739 hydrogen Inorganic materials 0.000 description 1
- 239000001257 hydrogen Substances 0.000 description 1
- 239000004615 ingredient Substances 0.000 description 1
- 238000003754 machining Methods 0.000 description 1
- 239000000463 material Substances 0.000 description 1
- 229910052758 niobium Inorganic materials 0.000 description 1
- 229910052760 oxygen Inorganic materials 0.000 description 1
- 239000001301 oxygen Substances 0.000 description 1
- 238000011946 reduction process Methods 0.000 description 1
- 238000011160 research Methods 0.000 description 1
- 238000005728 strengthening Methods 0.000 description 1
- 239000000725 suspension Substances 0.000 description 1
- 238000012360 testing method Methods 0.000 description 1
- 230000001550 time effect Effects 0.000 description 1
- 229910000859 α-Fe Inorganic materials 0.000 description 1
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Abstract
The invention discloses high-carbon cold-rolled automobile diaphragm spring steel. The high-carbon cold-rolled automobile diaphragm spring steel is prepared from the following constituents in percentage by weight: 0.70-0.90% of C, 0.15-0.35% of Si, 0.50-1.00% of Mn, P smaller than or equal to 0.008%, S smaller than or equal to 0.002%, 0.010-0.030% of Alt, 0.10-0.30% of V, 1.20-2.00% of Cr, 1.20-2.00% of Ni, 0.002-0.006% of Ca, and N smaller than or equal to 0.004%, and is prepared by the following production steps: molten iron desulphurization, smelting in a converter, refining in an LF (Ladle Furnace) furnace, processing in a RH vacuum furnace, continuous casting to form blanks, pit type slow cooling after cutting of cast blanks, cast blank heating, segmented hot rolling, reeling, slow cooling, annealing after cutting, cold rolling, quenching, tempering, and inspection for standby. The steel disclosed by the invention is rolled and thermally treated to achieve high strength, high elasticity, high limit of yielding, high fatigue limit resistance, low-temperature toughness and longer service life, and can be used for manufacturing various vehicle clutch assemblies, especially the large engineering machinery at the low temperature environment.
Description
Technical field
The present invention relates to spring steel, be specifically used for the cold rolling diaphragm spring steel of automobile and production method thereof.
Background technology
In automobile clutch assembly, diaphragm spring has a significant impact the performance and used life in automobile clutch assembly.At present, limitting by metallurgical equipment ability level and post-production level, the carbon content in domestic automobile diaphragm spring steel is not high, generally within 0.65%, and the operational path adopting " hot rolling → annealing → pickling → processing → thermal treatment " more.Mainly due to its carbon and chromium content low, make the mechanical property of product as intensity and hardness lower, and easy brittle failure under low temperature environment, can not meet the large-scale engineering machinery vehicle that uses at low temperature environment to the requirement of diaphragm spring.
Before the present invention proposes, the similar technique product relating to high-carbon cold rolled automobile steel making field is few, less particularly for high-carbon cold rolled automobile diaphragm spring steel aspect.
Through retrieval: Chinese Patent Application No. is the patent documentation of 201210462512, it discloses " a kind of automobile cold-rolled diaphragm spring steel and production method thereof ".Its composition and mass percentage content are: C:0.40 ~ 0.65%, Si:0.10 ~ 0.35%, Mn:0.60 ~ 1.00%, Cr:0.80 ~ 1.20%, Ni:0.20 ~ 0.50%, V:0.27 ~ 0.55%, P≤0.010%, S≤0.007%, and all the other are Fe and inevitable impurity.The document with the addition of a certain amount of Ni and Mn in chemical composition, but C content and Cr content on the low side, although there is reasonable cold-rolling workability energy, intensity, hardness, toughness are on the low side, can not meet low temperature environment use large-scale engineering machinery vehicle to the requirement of diaphragm spring.
Chinese Patent Application No. is the document of 94191328, it discloses " a kind of low decarburization for automotive suspension spring, high-toughness spring steel ", involved steel has following ingredients and mass percent: C:0.50 ~ 0.70%, Si:1.00 ~ 3.5%, Mn:0.30 ~ 1.50%, Cr:0.30 ~ 1.00%, Ni:0.50 ~ 5.00%, V:0.05 ~ 0.50%, P≤0.020%, S≤0.020%, all the other are Fe and inevitable impurity.In its chemical composition, C, Cr are on the low side, and its intensity, hardness, fatigue property and elastic limit are also on the low side; And because Si content is higher in this steel, also there is the deficiency of production and the increase of later stage cold and hot working risk of breakage.
Japanese Patent JP2507791A, JP3745193A and JPH06228734, be the spring steel for clutch diaphragm, and it with the addition of a certain amount of Mo in chemical composition, C content and Cr content still on the low side.It there is fatigue property and elastic limit is on the low side, and the Oxygen potential after annealing is also on the low side.In addition, because Si content is higher in steel, as produced wide steel strip, risk of breakage can be made comparatively large in post-production shear stage and cannot use.
In order to improve automobile diaphragm spring elastic force, cold and hot working performance, work-ing life further, reduce plate property fluctuation, meet the large-scale engineering machinery vehicle automobile diaphragm spring requirement that low temperature environment uses, the applicant researches and develops the present patent application.
Summary of the invention
The object of the invention is to overcome the deficiency that prior art exists, provide a kind of after quenching and tempering tensile strength at 1600 ~ 2400MPa, HRC at 47 ~ 59 ,-40 DEG C of KV
2>=34J, elastic limit high for the cold rolling diaphragm spring steel of automobile and production method thereof.
Realize the measure of above-mentioned purpose:
A kind of high-carbon cold rolled automobile diaphragm spring steel, its component and weight percent content are: C:0.70 ~ 0.90%, Si:0.15 ~ 0.35%, Mn:0.50 ~ 1.00%, P≤0.008%, S≤0.002%, Alt:0.010 ~ 0.030%, V:0.10 ~ 0.30%, Cr:1.20 ~ 2.00%, Ni:1.20 ~ 2.00%, Ca:0.002 ~ 0.006%, N≤0.004%, surplus is Fe and is inevitably mingled with; Metallographic structure is tempered martensite.
Produce a kind of method of high-carbon cold rolled automobile diaphragm spring steel, its step:
1) desulfurizing iron is carried out;
2) converter smelting is carried out;
3) in LF stove, refining is carried out;
4) process in RH vacuum oven, control vacuum processing time and be no less than 20 minutes;
5) continuous casting becomes base: in casting process, induction stirring all the time; And slighter compress is carried out to strand, draft is 2% ~ 8%;
6) strand carries out pit slow cooling and is cooled to room temperature after cutting;
7) to strand heating, heating and temperature control is 1200 ~ 1300 DEG C, and it is 8 ~ 14 minutes/centimetre that heating rate controls;
8) carry out segmentation hot rolling: control roughing start rolling temperature at 1050 ~ 1200 DEG C, control finish rolling finishing temperature at 800 ~ 900 DEG C;
9) batch, control coiling temperature at 700 ~ 800 DEG C;
10) carry out slow cooling, speed of cooling controls to be no more than 200 DEG C being no more than to be cooled under 15 DEG C/h;
11) anneal after cutting, annealing temperature is 750 ~ 850 DEG C, and annealing and soaking time are not less than 1550min;
12) carry out cold rolling, cold rolling pass is 1 ~ 3, and total reduction is 15 ~ 30%;
13) quench: control quenching temperature at 850 ~ 950 DEG C, Quenching Soaking Time is not less than 30min;
14) carry out tempering, control tempering temperature at 600 ~ 700 DEG C, tempering insulation time is not less than 50min; Metallographic structure after tempered is tempered martensite;
15) inspection and stand-by.
The function and mechanism of each element and main technologic parameters in the present invention:
Consider that this steel mainly will ensure high strength, snappiness, high yield strength, the highly anti-fatigue limit and comparatively long life, good shearing and cold-rolling workability energy must be possessed simultaneously.Therefore, strictly to control the purity of molten steel during steel-making, prevent P, S content on the impact of steel brittleness.The design mix of C, Si, Mn, Cr, Ni, V ensure that the scope such as intensity, elasticity, safe range of stress of steel meets the requirement of automobile diaphragm spring steel.Generally speaking, adopt on the combined microalloying of Cr, Ni, V and other elements, the feature of each element be given full play to.
Alloying element is on the impact of automobile diaphragm spring Steel Properties
C: it improves the most effective element of intensity, along with the increase of C content, Fe in steel
3c increases, and hardenability also increases, and the tensile strength of steel and yield strength improve.But along with C content increases, the unit elongation of steel, impelling strength and cold-forming property decline.Therefore, for ensureing that steel plate has high strength, high hardenability, high-wearing feature, C content controls within 0.70% ~ 0.90% by the present invention.If C content is too low, its intensity, hardness and wear resistance will decline, and not reach the design requirements of large-scale engineering machinery vehicle diaphragm spring.
Si: the avidity of itself and carbon is very weak, not carburet in steel, but can ferrite be dissolved in, produce solution strengthening effect, ferritic intensity and hardness are improved, but plasticity and toughness decline to some extent.Visible, Si has certain help to intensity, but content can not be too high, in order to avoid reduce the plasticity and toughness of steel.Consider that steel of the present invention will carry out cold rolling processing and intensity contribution, therefore Si content controls in 0.15 ~ 0.35% scope.
Mn: the avidity of itself and carbon is stronger, it is the effective element expanding austenite phase field, crystal grain thinning, spheroidized carbide and guarantee over-all properties and improve hardening capacity, and it does not worsen the deformability of steel, the Mn of 1.00% about can the intensity of tensile strength contribution 100MPa.The higher meeting of Mn content forms segregation line in steel, causes points hardness's intensity higher, is unfavorable for later stage cold rolling processing.Therefore consider that Mn is to intensity contribution and the drawback to tissue, controls Mn 0.50% ~ 1.00%.
Al is the main deoxidant element in steel, and the maxima solubility in austenite about 0.6%, it only faintly increases hardening capacity after dissolving in austenite.But when Al content is higher, easily cause being mingled with in steel increasing, unfavorable to the toughness of steel, hardenability and the toughness of steel can be reduced simultaneously, reduce the work-ing life of spring steel.Therefore Alt content in steel is controlled within 0.030%.
Cr can improve the hardening capacity of steel, is the element effectively improving steel strength particularly hot strength, can also improves cementite stability and hardness in steel, plays an important role to improving the elasticity of steel, wear resistance and ultimate strength.Material anti-hydrogen embrittlement ability, improves steel temper resistance.Consider above-mentioned analytical results, Cr content is controlled 1.20% ~ 2.00%.
Ni can not form carbide, is the effective element expanding γ phase, crystal grain thinning, spheroidized carbide and guarantee over-all properties and improve hardening capacity, improves the pearlitic spheroidization ratio after annealing, be convenient to cold and hot working.Meanwhile, the toughness of coil of strip can be significantly improved after adding Ni.Therefore, Ni content is controlled 1.20% ~ 2.00%.
V is effective one of carbide forming element improving armor plate strength, and the effect in steel is only second to Nb, Ti.To VC be formed after adding V in steel, improve the fusing point of cementite, hardness and wear resistance.But the content of V can not be too high, there is disperse state distribution in V, produces secondary hardening, be unfavorable for the inspection during manufacture of steel when average tempering.Therefore, when the present invention designs the content of V, V is controlled 0.10% ~ 0.30%.
(2) impurity element and gas are on the impact of automobile diaphragm spring Steel Properties
Cold rolled automobile diaphragm spring steel need guarantee the cold-rolling workability energy of steel, and the cold-forming property of impurity element to steel in steel has a significant impact.Although P, S content in steel is very few, comparatively large on cold-forming property impact, strict its content of control obviously can reduce the phenomenon of rupture in the course of processing.Often caused by the expansion of formation of crack in the brittle failure of cold-rolled steel coils generation, formation of crack then appears at segregation place of P mostly, and also easily causes layering to tear containing the segregation of the inclusion of S.Therefore, should control within 0.008% by P for this steel, S controls within 0.002%.
In addition, this steel continuous casting and slow cooling process entails higher, gas content in steel should be reduced as far as possible, reduce the segregation of steel.Meanwhile, in order to reduce the influence of time effect of steel, the content of N is controlled within 0.004%.
The reason of production technique setting
(1) process for making
During this smelting steel, vacuum processing time is not less than 20min, can reduce impurity in steel, gas content preferably.Carbon Content Of Steel, alloying element content are higher, must carry out induction stirring and dynamic soft-reduction process before continuous casting, reduce element segregation.
(2) steel rolling process
Because this hardness of steel is high, be rolled by high-strength steel technique and batch.Before rolling, slab heating temperature is 1200 ~ 1300 DEG C, guarantees strand homogeneous temperature.When roughing and finish rolling, design temperature is higher than conventional low alloy steel, reduces milling equipment load.Meanwhile, the critical point temperature of steel be considered, avoid occurring mixed crystal phenomenon.Therefore, the roughing start rolling temperature of steel is 1050 ~ 1200 DEG C, and finish rolling finishing temperature is 900 ~ 950 DEG C, and coiling temperature is 700 ~ 800 DEG C.Batching and carry out retarded cooling process to coil of strip afterwards, is batch internal stress to reduce and make coil of strip different sites mechanical property even.
(3) thermal treatment process
Because product finally needs to be processed into automobile clutch disk, and require higher to quality product, so for the feature Design and Machining operational path of this steel: cutting → annealing → pickling → cold rolling → quenching → tempering → inspection is delivered.It is in order to the coil of strip intensity that declines to a great extent that annealing temperature is designed to 750 ~ 850 DEG C, and makes the pearlitic structure nodularization of steel and evenly, be easy to shearing.Quenching temperature is designed to 850 ~ 950 DEG C, tempering temperature is designed to 600 ~ 700 DEG C, be to allow steel complete austenitizing, obtaining uniform and stable tempered martensite after quenching+tempering, obtain high strength, snappiness, high yield strength, the highly anti-fatigue limit and comparatively long life.
Steel tool of the present invention has the following advantages:
Composition Design adopts high-carbon, and adds a certain amount of Mn, Cr, V, simultaneously strict control P, S content, make this steel have excellent comprehensive mechanical property.Utilize rational rolling and batch system, in mill milling limit of power, improving coil of strip performance.The operational path of hot rolled coil → annealing → pickling → cutting → processing → quenching → tempering is devised in post-production, annealing process is utilized to reduce shearing difficulty, and obtain back martensitic stucture by quenching+tempering thermal treatment, utilize the complex intensifying effect of the microalloy such as Mn, Ni, V in steel to ensure that steel obtain enough intensity and wear resistance.
Steel of the present invention by after rolling and thermal treatment, tensile strength at 1600 ~ 2400MPa, HRC at 47 ~ 59 ,-40 DEG C of KV
2>=34J, namely has high strength, snappiness, high yield strength, the highly anti-fatigue limit, low-temperature flexibility and comparatively long life, can be used for manufacturing various types of vehicles clutch assembly, is particularly applicable to the large-scale engineering machinery vehicle under low temperature environment.
Accompanying drawing explanation
Fig. 1 is As rolled metallographic structure figure of the present invention;
Fig. 2 is Annealed microstructure metallographic structure figure of the present invention;
Fig. 3 is quenching+tempering state metallographic structure figure of the present invention.
Embodiment
Below the present invention is described in detail:
Table 1 is the value list of various embodiments of the present invention and comparative example;
Table 2 is the main technologic parameters list of various embodiments of the present invention and comparative example;
Table 3 is various embodiments of the present invention and comparative example mechanical properties test the results list.
Various embodiments of the present invention are produced according to following steps:
1) desulfurizing iron is carried out;
2) converter smelting is carried out;
3) in LF stove, refining is carried out;
4) process in RH vacuum oven, control vacuum processing time and be no less than 20 minutes;
5) continuous casting becomes base: in casting process, induction stirring all the time; And slighter compress is carried out to strand, draft is 2% ~ 8%;
6) strand carries out pit slow cooling and is cooled to room temperature after cutting;
7) to strand heating, heating and temperature control is 1200 ~ 1300 DEG C, and it is 8 ~ 14 minutes/centimetre that heating rate controls;
8) carry out segmentation hot rolling: control roughing start rolling temperature at 1050 ~ 1200 DEG C, control finish rolling finishing temperature and exist
800 ~ 900 DEG C;
9) batch, control coiling temperature at 700 ~ 800 DEG C;
10) carry out slow cooling, speed of cooling controls to be no more than 200 DEG C being no more than to be cooled under 15 DEG C/h;
11) anneal after cutting, annealing temperature is 750 ~ 850 DEG C, and annealing and soaking time are not less than 1550min;
12) carry out cold rolling, cold rolling pass is 1 ~ 3, and total reduction is 15 ~ 30%;
13) quench: control quenching temperature at 850 ~ 950 DEG C, Quenching Soaking Time is not less than 30min;
14) carry out tempering, control tempering temperature at 600 ~ 700 DEG C, tempering insulation time is not less than 50min; Metallographic structure after tempered is tempered martensite;
15) inspection and stand-by.
Table 1 various embodiments of the present invention and compared steel chemical composition (wt%)
The main processes of table 2 embodiment of the present invention and comparative example
Table 3 embodiment of the present invention and the heat treatment process contrasting steel grade
Note: table 1 is not one-to-one relationship to each embodiment value of table 3.
The mechanics assay of table 4 embodiment of the present invention and comparative example
As can be seen from Table 4, steel grade of the present invention has high strength (R
m: 1600 ~ 2400MPa), snappiness, high yield strength and the highly anti-fatigue limit, have good cold-rolling workability can and low-temperature flexibility level (-40 DEG C of KV
2>=34J), can be used for the large-scale engineering machinery vehicle manufacturing various types of vehicles clutch assembly, particularly low temperature environment service requirements.
Above-described embodiment is only the best and exemplifies, and is not the restriction to embodiments of the present invention.
Claims (2)
1. a high-carbon cold rolled automobile diaphragm spring steel, its component and weight percent content are: C:0.70 ~ 0.90%, Si:0.15 ~ 0.35%, Mn:0.50 ~ 1.00%, P≤0.008%, S≤0.002%, Alt:0.010 ~ 0.030%, V:0.10 ~ 0.30%, Cr:1.20 ~ 2.00%, Ni:1.20 ~ 2.00%, Ca:0.002 ~ 0.006%, N≤0.004%, surplus is Fe and is inevitably mingled with; Metallographic structure is tempered martensite.
2. produce a kind of method of high-carbon cold rolled automobile diaphragm spring steel, its step:
1) desulfurizing iron is carried out;
2) converter smelting is carried out;
3) in LF stove, refining is carried out;
4) process in RH vacuum oven, control vacuum processing time and be no less than 20 minutes;
5) continuous casting becomes base: in casting process, induction stirring all the time; And slighter compress is carried out to strand, draft is 2% ~ 8%;
6) strand carries out pit slow cooling and is cooled to room temperature after cutting;
7) to strand heating, heating and temperature control is 1200 ~ 1300 DEG C, and it is 8 ~ 14 minutes/centimetre that heating rate controls;
8) carry out segmentation hot rolling: control roughing start rolling temperature at 1050 ~ 1200 DEG C, control finish rolling finishing temperature at 800 ~ 900 DEG C;
9) batch, control coiling temperature at 700 ~ 800 DEG C;
10) carry out slow cooling, speed of cooling controls to be no more than 200 DEG C being no more than to be cooled under 15 DEG C/h;
11) anneal after cutting, annealing temperature is 750 ~ 850 DEG C, and annealing and soaking time are not less than 1550min;
12) carry out cold rolling, cold rolling pass is 1 ~ 3, and total reduction is 15 ~ 30%;
13) quench: control quenching temperature at 850 ~ 950 DEG C, Quenching Soaking Time is not less than 30min;
14) carry out tempering, control tempering temperature at 600 ~ 700 DEG C, tempering insulation time is not less than 50min; Metallographic structure after tempered is tempered martensite;
15) inspection and stand-by.
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| CN107419196A (en) * | 2017-09-18 | 2017-12-01 | 东北大学 | Manganese automobile steel and preparation method thereof in the easily welding of the controllable Ultra-low carbon of yield tensile ratio |
| CN107709597A (en) * | 2015-07-27 | 2018-02-16 | 新日铁住金株式会社 | Bearing spring steel and its manufacture method |
| CN108817338A (en) * | 2018-07-06 | 2018-11-16 | 青岛特殊钢铁有限公司 | A kind of continuous casting and rolling process for production suitable for high-strength spring flat steel |
| CN111315901A (en) * | 2017-11-07 | 2020-06-19 | Posco公司 | High-strength low-toughness cold-rolled steel sheet having excellent fracture characteristics and method for producing same |
| CN114107841A (en) * | 2022-01-27 | 2022-03-01 | 北京科技大学 | High-strength corrosion-resistant spring steel and preparation method thereof |
| CN114574770A (en) * | 2022-03-05 | 2022-06-03 | 新疆八一钢铁股份有限公司 | Preparation method of high-strength fatigue-resistant 60Si2MnA spring steel |
| CN114807555A (en) * | 2022-04-19 | 2022-07-29 | 安阳钢铁集团有限责任公司 | Production method of high-carbon high-silicon spring steel hot continuous rolling steel strip |
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