CN104313472A - High-carbon hot-rolled automobile diaphragm spring steel and production method thereof - Google Patents
High-carbon hot-rolled automobile diaphragm spring steel and production method thereof Download PDFInfo
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- CN104313472A CN104313472A CN201410602968.1A CN201410602968A CN104313472A CN 104313472 A CN104313472 A CN 104313472A CN 201410602968 A CN201410602968 A CN 201410602968A CN 104313472 A CN104313472 A CN 104313472A
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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
- C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium 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
- C22C33/00—Making ferrous alloys
- C22C33/04—Making ferrous alloys by melting
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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
- C22C38/04—Ferrous alloys, e.g. steel alloys containing 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
- C22C38/06—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
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Abstract
The invention discloses high-carbon hot-rolled automobile diaphragm spring steel. The high-carbon hot-rolled automobile diaphragm spring steel is prepared from the following constituents in percentage by weight: 0.70-0.90% of C, Si smaller than or equal to 0.10%, Mn smaller than or equal to 0.80%, P smaller than or equal to 0.008%, S smaller than or equal to 0.003%, 0.010-0.030% of Alt, 1.20-1.80% of Cr, 0.10-0.30% of V, 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 an 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, quenching, tempering, and inspection for standby. The steel disclosed by the invention is quenched and tempered to achieve tensile strength of 1600-2200 MPa, HRC (Rockwell Hardness) of 47-57, high limit of elasticity, high limit of yielding, high fatigue limit resistance and longer service life, and can be used for manufacturing various vehicle clutch assemblies for large engineering machinery.
Description
Technical field
The present invention relates to spring steel, be specifically used for automobile hot rolling diaphragm spring steel 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 not high in intensity and hardness, it can not meet the vehicle diaphragm spring Future Development service requirementss such as large-scale engineering machinery car.
Before the present invention proposes, the similar technique product relating to high-carbon Hot Rolling Automobile steel making field is few, less particularly for high-carbon Hot Rolling Automobile diaphragm spring steel aspect.
Through retrieval: Chinese Patent Application No. is the patent documentation of CN201210462046.6, it discloses " a kind of automobile hot rolling diaphragm spring steel and production method thereof " number of patent application CN201210462046.6, involved steel has following ingredients and mass percent C:0.40% ~ 0.60%, Si:0.15% ~ 0.35%, Mn:0.70% ~ 1.20%, Cr:0.70% ~ 1.20%, V:0.10 ~ 0.50%, P≤0.015%, S≤0.008%, all the other are Fe and inevitable impurity.This hot rolled strip is compared with the present invention, and chemical composition with the addition of a certain amount of Cr, and C content is on the low side, although comprehensive mechanical property is outstanding, but after thermal treatment, hardness and toughness do not reach design requirements.
Have three Japanese Patents JP2507791A, JP3745193A and JPH06228734, be clutch diaphragm spring steel, these steel are compared with invention steel, chemical composition with the addition of a certain amount of Mo, C content is on the low side, and Si, Mn upper content limit is higher, adds the alloys such as a certain amount of V, Nb, Cr simultaneously.This steel is compared with invention steel, and intensity is higher, and during production, rolling load is comparatively large, requires higher to production unit.In addition, because Si content is higher in steel, as produced wide steel strip, post-production shear fracture risk is larger.
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 diaphragm spring requirement of development, 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 ~ 2200MPa, HRC 47 ~ 57, elastic limit high for automobile hot rolling diaphragm spring steel and production method thereof.
Realize the measure of above-mentioned purpose:
A kind of high-carbon Hot Rolling Automobile diaphragm spring steel, its component and weight percent content are: C:0.70 ~ 0.90%, Si≤0.10%, Mn :≤0.80%, P≤0.008%, S≤0.003%, Alt:0.010 ~ 0.030%, Cr:1.20 ~ 1.80%, V:0.10 ~ 0.30%, 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 Hot Rolling 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 be 2% ~ 8% to depress strand at draft;
6) strand carries out pit slow cooling after cutting, and is cooled to room temperature;
7) to the strand heating after cutting, 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 900 ~ 950 DEG C;
9) batch, control coiling temperature at 700 ~ 800 DEG C;
10) carry out slow cooling, be cooled under speed of cooling is no more than 20 DEG C/h and be no more than 200 DEG C;
11) anneal, annealing temperature is 750 ~ 850 DEG C, and annealing and soaking time are not less than 1550min;
12) quench: control quenching temperature at 850 ~ 950 DEG C, Quenching Soaking Time is not less than 30min;
13) 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;
14) 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, 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, 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, therefore Si content controls in≤0.10% 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 Mn is controlled≤0.80%.
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% ~ 1.80%.Why to improve the content of chromium? what problem that prior art exists can be solved?
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 0.003%.
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.After strand cutting, necessary slow cooling, avoids high-temperature embrittlement region, prevents disconnected base.
(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 after quenching and tempering tensile strength at 1600 ~ 2200MPa, HRC 47 ~ 57, the high yield strength of elastic limit, the highly anti-fatigue limit and comparatively long life, can be used for manufacturing all kinds of large-scale engineering machinery vehicular clutch assembly.
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 be 2% ~ 8% to depress strand at draft;
6) strand carries out pit slow cooling after cutting, and is cooled to room temperature;
7) to the strand heating after cutting, 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 900 ~ 950 DEG C;
9) batch, control coiling temperature at 700 ~ 800 DEG C;
10) carry out slow cooling, be cooled under speed of cooling is no more than 20 DEG C/h and be no more than 200 DEG C;
11) anneal, annealing temperature is 750 ~ 850 DEG C, and annealing and soaking time are not less than 1550min;
12) quench: control quenching temperature at 850 ~ 950 DEG C, Quenching Soaking Time is not less than 30min;
13) 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;
14) 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 ~ 2200MPa), snappiness, high yield strength and the highly anti-fatigue limit, have good cold-rolling workability energy, can be used for manufacturing various types of vehicles clutch assembly, particularly heavy-duty truck.
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 Hot Rolling Automobile diaphragm spring steel, its component and weight percent content are: C:0.70 ~ 0.90%, Si≤0.10%, Mn :≤0.80%, P≤0.008%, S≤0.003%, Alt:0.010 ~ 0.030%, Cr:1.20 ~ 1.80%, V:0.10 ~ 0.30%, 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 Hot Rolling 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 be 2% ~ 8% to depress strand at draft;
6) strand carries out pit slow cooling after cutting, and is cooled to room temperature;
7) to the strand heating after cutting, 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 900 ~ 950 DEG C;
9) batch, control coiling temperature at 700 ~ 800 DEG C;
10) carry out slow cooling, be cooled under speed of cooling is no more than 20 DEG C/h and be no more than 200 DEG C;
11) anneal, annealing temperature is 750 ~ 850 DEG C, and annealing and soaking time are not less than 1550min;
12) quench: control quenching temperature at 850 ~ 950 DEG C, Quenching Soaking Time is not less than 30min;
13) 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;
14) inspection and stand-by.
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| CN201410602968.1A CN104313472B (en) | 2014-10-31 | 2014-10-31 | A kind of high-carbon Hot Rolling Automobile diaphragm spring steel and production method thereof |
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Cited By (6)
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| CN107709597A (en) * | 2015-07-27 | 2018-02-16 | 新日铁住金株式会社 | Bearing spring steel and its manufacture method |
| CN108611572A (en) * | 2018-05-11 | 2018-10-02 | 鞍钢股份有限公司 | A kind of high-ductility hypereutectoid steel spring plate and its production method |
| CN111676422A (en) * | 2020-06-17 | 2020-09-18 | 苏州翔楼新材料股份有限公司 | Cold-rolled high-carbon steel strip for V-saw blade matrix and production method thereof |
| CN114875326A (en) * | 2022-05-21 | 2022-08-09 | 湖南华菱湘潭钢铁有限公司 | Production method of flat spring steel |
| CN115094304A (en) * | 2022-05-10 | 2022-09-23 | 江阴兴澄特种钢铁有限公司 | Steel for producing ball screw with ultra-long service life by continuous casting round billet and preparation method thereof |
| CN115874108A (en) * | 2022-12-21 | 2023-03-31 | 湖南华菱涟源钢铁有限公司 | Method for refining dendritic crystal structure in steel |
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Cited By (9)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN107709597A (en) * | 2015-07-27 | 2018-02-16 | 新日铁住金株式会社 | Bearing spring steel and its manufacture method |
| EP3330399A4 (en) * | 2015-07-27 | 2019-03-27 | Nippon Steel & Sumitomo Metal Corporation | Steel for suspension spring and method for manufacturing same |
| CN107709597B (en) * | 2015-07-27 | 2019-08-27 | 日本制铁株式会社 | Bearing spring steel and its manufacturing method |
| CN108611572A (en) * | 2018-05-11 | 2018-10-02 | 鞍钢股份有限公司 | A kind of high-ductility hypereutectoid steel spring plate and its production method |
| CN111676422A (en) * | 2020-06-17 | 2020-09-18 | 苏州翔楼新材料股份有限公司 | Cold-rolled high-carbon steel strip for V-saw blade matrix and production method thereof |
| CN115094304A (en) * | 2022-05-10 | 2022-09-23 | 江阴兴澄特种钢铁有限公司 | Steel for producing ball screw with ultra-long service life by continuous casting round billet and preparation method thereof |
| CN115094304B (en) * | 2022-05-10 | 2023-09-15 | 江阴兴澄特种钢铁有限公司 | Steel for producing ultra-long-service-life ball screw by continuous casting round billet and preparation method thereof |
| CN114875326A (en) * | 2022-05-21 | 2022-08-09 | 湖南华菱湘潭钢铁有限公司 | Production method of flat spring steel |
| CN115874108A (en) * | 2022-12-21 | 2023-03-31 | 湖南华菱涟源钢铁有限公司 | Method for refining dendritic crystal structure in steel |
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