CN104313483B - A kind of high-carbon cold rolled automobile diaphragm spring steel and production method thereof - Google Patents
A kind of 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 18
- 229910052799 carbon Inorganic materials 0.000 title claims abstract description 17
- 238000004519 manufacturing process Methods 0.000 title abstract description 14
- 239000010959 steel Substances 0.000 claims abstract description 62
- 229910000831 Steel Inorganic materials 0.000 claims abstract description 61
- 238000000137 annealing Methods 0.000 claims abstract description 18
- 238000000034 method Methods 0.000 claims abstract description 17
- 238000010791 quenching Methods 0.000 claims abstract description 16
- 238000005097 cold rolling Methods 0.000 claims abstract description 15
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims abstract description 13
- 230000008569 process Effects 0.000 claims abstract description 13
- 230000000171 quenching effect Effects 0.000 claims abstract description 13
- 238000005096 rolling process Methods 0.000 claims abstract description 13
- 238000005496 tempering Methods 0.000 claims abstract description 11
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 10
- 229910052759 nickel Inorganic materials 0.000 claims abstract description 9
- 229910052698 phosphorus Inorganic materials 0.000 claims abstract description 9
- 229910052717 sulfur Inorganic materials 0.000 claims abstract description 9
- 229910052720 vanadium Inorganic materials 0.000 claims abstract description 9
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 8
- 238000010583 slow cooling Methods 0.000 claims abstract description 8
- 238000005266 casting Methods 0.000 claims abstract description 7
- 238000007689 inspection Methods 0.000 claims abstract description 6
- 229910052710 silicon Inorganic materials 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
- 230000003009 desulfurizing effect Effects 0.000 claims abstract description 4
- 229910052742 iron Inorganic materials 0.000 claims abstract description 4
- 230000011218 segmentation Effects 0.000 claims abstract description 4
- 238000001291 vacuum drying Methods 0.000 claims abstract description 4
- 229910052757 nitrogen Inorganic materials 0.000 claims abstract description 3
- 238000010438 heat treatment Methods 0.000 claims description 10
- 238000012545 processing Methods 0.000 claims description 10
- 229910000734 martensite Inorganic materials 0.000 claims description 7
- 230000009467 reduction Effects 0.000 claims description 6
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- 238000009413 insulation Methods 0.000 claims description 3
- 230000014759 maintenance of location Effects 0.000 claims description 3
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- 241000416536 Euproctis pseudoconspersa Species 0.000 claims 1
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims 1
- 230000002929 anti-fatigue Effects 0.000 abstract description 5
- 238000005520 cutting process Methods 0.000 abstract description 4
- 239000011651 chromium Substances 0.000 description 12
- 239000000203 mixture Substances 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
- 229910001566 austenite Inorganic materials 0.000 description 4
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- 239000013078 crystal Substances 0.000 description 3
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- 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
- 238000010008 shearing Methods 0.000 description 2
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- 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
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- 229910000859 α-Fe Inorganic materials 0.000 description 1
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Abstract
A kind of high-carbon cold rolled automobile diaphragm spring steel, its component and wt% be: 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%；Production stage: desulfurizing iron；Converter smelting；LF stove refines；RH vacuum drying oven processes；It is casting continuously to form base；Pit slow cooling is carried out after strand is cleaved；Strand heats；Segmentation hot rolling；Batch；Slow cooling；Cutting after annealing；Cold rolling；Quenching；Tempering；Inspection is the most stand-by.After steel of the present invention is by rolling and being heat-treated, there is high intensity, high resiliency, high yield limit, the highly anti-fatigue limit, low-temperature flexibility and long service life, can be used for manufacturing various types of vehicles clutch assembly, the large-scale engineering machinery vehicle being particularly suitable under low temperature environment.
Description
Technical field
The present invention relates to spring steel, be specifically used for automobile cold rolling diaphragm spring steel and production method thereof.
Background technology
In automobile clutch assembly, diaphragm spring has the biggest shadow to the performance and used life in automobile clutch assembly
Ring.At present, being limited by metallurgical equipment ability level and post-production level, the carbon content in domestic automobile diaphragm spring steel is not
Height, typically within 0.65%, and uses the process route of " hot rolling → annealing → pickling → processing → heat treatment " more.Mainly by
Low in its carbon and chromium content, the mechanical property such as intensity and hardness that make product are relatively low, and easy brittle failure under low temperature environment, it is impossible to meet
In the large-scale engineering machinery vehicle requirement to diaphragm spring that low temperature environment uses.
Before the present invention proposes, the similar technique product relating to high-carbon cold rolled automobile steel making field is few, particularly
Less in terms of high-carbon cold rolled automobile diaphragm spring steel.
Through retrieval: Chinese Patent Application No. is the patent document of 201210462512, it discloses " a kind of automobile cold-rolled
Diaphragm spring steel and production method thereof ".Its composition and mass percentage content be: 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%,
Remaining is 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 contain
Measure on the low side, although have reasonable cold-rolling workability energy, but intensity, hardness, toughness are on the low side, it is impossible to meet and use at low temperature environment
The requirement to diaphragm spring of the large-scale engineering machinery vehicle.
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 a 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%, remaining
For Fe and inevitable impurity.In its chemical composition, C, Cr are on the low side, and its intensity, hardness, fatigue behaviour and elastic limit are the most inclined
Low；And because Si content is higher in this steel, there is also and produce and the deficiency of later stage cold and hot working risk of breakage increase.
Japan Patent JP2507791A, JP3745193A and JPH06228734, be the spring for clutch diaphragm
Steel, it is the most on the low side that it with the addition of a certain amount of Mo, C content and Cr content in chemical composition.There is fatigue behaviour and elastic pole in it
Limiting on the low side, the Oxygen potential after annealing is the most on the low side.Additionally, because Si content is higher in steel, as produced wide flat steel, cut in post-production
The stage of cutting can make risk of breakage relatively big and cannot use.
In order to improve further automobile diaphragm spring elastic force, cold and hot working performance, service life, reduce plate property ripple
Dynamic, 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
It is an object of the invention to the deficiency overcoming prior art to exist, it is provided that tensile strength after a kind of quenched and tempering
At 1600 ~ 2400MPa, HRC at 47 ~ 59 ,-40 DEG C of KV2>=34J, elastic limit high for automobile cold rolling diaphragm spring steel
And production method.
Realize the measure of above-mentioned purpose:
A kind of high-carbon cold rolled automobile diaphragm spring steel, its component and weight percent content be: 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 inevitably presss from both sides
Miscellaneous；Metallographic structure is tempered martensite.
A kind of method producing high-carbon cold rolled automobile diaphragm spring steel, its step:
1) desulfurizing iron is carried out；
2) converter smelting is carried out；
3) refine in LF stove；
4) process in RH vacuum drying oven, control vacuum processing time no less than 20 minutes；
5) it is casting continuously to form base: electromagnetic agitation is all the time in casting process；And strand is carried out slighter compress, reduction ratio is 2% ~ 8%；
6) carry out pit slow cooling after strand is cleaved and be cooled to room temperature；
7) heating strand, heating and temperature control is 1200～1300 DEG C, and it is 8～14 minutes/centimetre that the rate of heat addition controls；
8) carry out segmentation hot rolling: control roughing start rolling temperature at 1050～1200 DEG C, control finish rolling finishing temperature 800～
900℃；
9) batch, control coiling temperature at 700～800 DEG C；
10) carrying out slow cooling, cooling velocity controls to be cooled under less than 15 DEG C/h less than 200 DEG C；
11) annealing after cleaved, annealing temperature is 750～850 DEG C, and annealing and temperature retention time are not less than 1550min；
12) carrying out cold rolling, cold rolling pass is 1 ~ 3, and total reduction is 15 ~ 30%；
13) quench: control hardening heat is at 850～950 DEG C, and Quenching Soaking Time is not less than 30min；
14) being tempered, control temperature is at 600～700 DEG C, and tempering insulation time is not less than 50min；After tempered
Metallographic structure be tempered martensite；
15) inspection and stand-by.
Each element and the effect of main technologic parameters and mechanism in the present invention:
Consider that this steel is mainly to ensure that high intensity, high resiliency, high yield limit, the highly anti-fatigue limit and longer use longevity
Life, must possess good shearing and cold-rolling workability energy simultaneously.Therefore, strictly to control the degree of purity of molten steel during steel-making, anti-
Only P, S content impact on steel brittleness.Being designed to of C, Si, Mn, Cr, Ni, V point ensure that the intensity of steel, elasticity, fatigue limit
The requirement of automobile diaphragm spring steel is met etc. scope.Generally speaking, Cr, Ni, V and the combined microalloying of other elements are used
On, the feature of each element will be given full play to.
The alloying element impact on automobile diaphragm spring Steel Properties
C: it is to improve the maximally effective element of intensity, along with the increase of C content, Fe in steel3C increases, and hardenability also increases,
The tensile strength of steel and yield strength improve.But, along with C content increases, the elongation percentage of steel, impact flexibility and cold-workability
Can decline.Therefore, for ensureing that steel plate has high intensity, high hardenability, high-wearing feature, C content controls 0.70% by the present invention ~
Within 0.90%.If C content is too low, its intensity, hardness and wearability will decline, and not reach large-scale engineering machinery vehicle diaphragm
Spring design requirement.
Si: it is the most weak with the affinity of carbon, not carburet in steel, but ferrite can be dissolved in, produce solution strengthening and make
With so that ferritic intensity and hardness improve, but plasticity and toughness have declined.Visible, Si has certain help to intensity,
But content can not be too high, in order to avoid reducing the plasticity and toughness of steel.Consider that steel of the present invention to carry out cold rolling processing and intensity contribution, therefore Si contains
Amount controls in the range of 0.15 ~ 0.35%.
Mn: it is relatively strong with the affinity of carbon, is that expansion austenite phase field, crystal grain thinning, spheroidized carbide and guarantee are comprehensive
Performance and improve the effective element of quenching degree, and it does not deteriorate the deformability of steel, the Mn of 1.00% about can tensile strength tribute
Offer the intensity of 100MPa.The higher meeting of Mn content forms segregated zone in steel, causes points hardness's intensity higher, is unfavorable for that the later stage is cold
Roll processing.Therefore in view of Mn to intensity contribution and the drawback to tissue, Mn is controlled 0.50% ~ 1.00%.
Al is the main deoxidant element in steel, and the maxima solubility in austenite about 0.6%, after it dissolves in austenite
Only weakly increase quenching degree.But when Al content is higher, it is easily caused in steel to be mingled with and increases, unfavorable to the toughness of steel, simultaneously
Hardenability and the toughness of steel can be reduced, reduce the service life of spring steel.Therefore Alt content in steel is controlled 0.030% with
In.
Cr can improve the quenching degree of steel, is the element being effectively improved steel strength particularly elevated temperature strength, moreover it is possible to improves steel
Middle cementite stability and hardness, play an important role to improving the elasticity of steel, wearability and ultimate strength.Material anti-hydrogen embrittlement ability,
Improve steel temper resistance.In view of above-mentioned analysis result, Cr content is controlled 1.20% ~ 2.00%.
Ni will not form carbide, is to expand γ phase, crystal grain thinning, spheroidized carbide and guarantee combination property and raising
The effective element of quenching degree, improves the pearlitic spheroidization ratio after annealing, it is simple to cold and hot working.Meanwhile, can be obvious after adding Ni
Improve the toughness of coil of strip.Therefore, Ni content is controlled 1.20% ~ 2.00%.
V is one of carbide former being effectively improved armor plate strength, and the effect in steel is only second to Nb, Ti.In steel
VC will be formed after adding V, improve the fusing point of cementite, hardness and wearability.But the content of V can not be too high, and V is at average tempering
Shi Fasheng disperse state is distributed, and produces post-curing, is unfavorable for the inspection during manufacture of steel.Therefore, the present invention will when designing the content of V
V controls 0.10% ~ 0.30%.
(2) impurity element and the gas impact on automobile diaphragm spring Steel Properties
Cold rolled automobile diaphragm spring steel need to guarantee steel cold-rolling workability can, and the cold working that the impurity element in steel is to steel
Performance has a significant impact.Although P, S content in steel is the fewest, but relatively big on cold-forming property impact, strict its content energy of control
Significantly reduce the phenomenon of rupture in process.Brittle failure in cold-rolled steel coils generation is often caused by the extension of formation of crack, splits
Line source occurs at the segregation of P the most mostly, and the segregation of the field trash containing S also easily causes layering tear etc..Therefore, for this steel
Should control within 0.008% by P, S controls within 0.002%.
It addition, this steel requires higher at continuous casting and annealing process, gas content in steel should be reduced as far as possible, reduce the inclined of steel
Analysis.Meanwhile, in order to reduce the influence of time effect of steel, the content of N is controlled within 0.004%.
The reason that production technology sets
(1) process for making
During this steel smelting, vacuum processing time is not less than 20min, can preferably reduce impurity in steel, gas content.Steel contains
Carbon amounts, alloying element content are higher, must carry out electromagnetic agitation and dynamic soft-reduction processes, reduce element segregation before continuous casting.
(2) steel rolling process
Owing to this hardness of steel is high, to roll by high-strength steel technique and batch.Before rolling slab heating temperature be 1200 ~
1300 DEG C, it is ensured that 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 to be considered, it is to avoid mixed crystal phenomenon occurs.Therefore, the roughing start rolling temperature of steel be 1050 ~
1200 DEG C, finish rolling finishing temperature is 900 ~ 950 DEG C, and coiling temperature is 700 ~ 800 DEG C.After batching, coil of strip is carried out retarded cooling process,
It is to batch internal stress to reduce and make coil of strip different parts mechanical property uniform.
(3) Technology for Heating Processing
Finally need to be processed into automobile clutch disk due to product, and product quality is required higher, so for this
The feature design machining process route of steel: cutting → annealing → pickling → cold rolling → quenching → tempering → inspection delivery.Annealing temperature
It is for the coil of strip intensity that declines to a great extent that degree is designed as 750 ~ 850 DEG C, and makes the pearlitic structrure nodularization and uniformly of steel, it is easy to cut
Cut processing.Hardening heat is designed as 850 ~ 950 DEG C, and temperature is designed as 600 ~ 700 DEG C, is to allow the complete austenite of steel
Change, obtain uniform and stable tempered martensite after quenching+tempering, it is thus achieved that high intensity, high resiliency, high yield limit, highly anti-fatigue
The limit and long service life.
Steel of the present invention has the advantage that
Composition design uses high-carbon, and adds a certain amount of Mn, Cr, V, strictly control P, S content simultaneously so that should
Steel has excellent comprehensive mechanical property.Utilize and reasonably roll and batch system, in mill milling limit of power, improve steel
Volume performance.Post-production devises the process route of hot rolled coil → annealing → pickling → cutting → processing → quenching → tempering,
Utilize annealing process to reduce shearing difficulty, and be thermally treated resulting in back martensitic structure by quenching+tempering, utilize Mn in steel,
The complex intensifying effect of the microalloies such as Ni, V ensure that steel obtain enough intensity and wearability.
Steel of the present invention by rolling and be heat-treated after, tensile strength at 1600 ~ 2400MPa, HRC at 47 ~ 59 ,-40 DEG C of KV2
>=34J, i.e. has high intensity, high resiliency, high yield limit, the highly anti-fatigue limit, low-temperature flexibility and long service life, available
In manufacturing various types of vehicles clutch assembly, the large-scale engineering machinery vehicle being particularly suitable under low temperature environment.
Accompanying drawing explanation
Fig. 1 is the rolled metallographic structure figure of the present invention；
Fig. 2 is the Annealed microstructure metallographic structure figure of the present invention；
Fig. 3 is the quenching+tempering state metallographic structure figure of the present invention.
Detailed description of the invention
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 produce according to following steps:
1) desulfurizing iron is carried out；
2) converter smelting is carried out；
3) refine in LF stove；
4) process in RH vacuum drying oven, control vacuum processing time no less than 20 minutes；
5) it is casting continuously to form base: electromagnetic agitation is all the time in casting process；And strand is carried out slighter compress, reduction ratio is 2% ~ 8%；
6) carry out pit slow cooling after strand is cleaved and be cooled to room temperature；
7) heating strand, heating and temperature control is 1200～1300 DEG C, and it is 8～14 minutes/centimetre that the rate of heat addition controls；
8) carry out segmentation hot rolling: control roughing start rolling temperature at 1050～1200 DEG C, control finish rolling finishing temperature 800～
900℃；
9) batch, control coiling temperature at 700～800 DEG C；
10) carrying out slow cooling, cooling velocity controls to be cooled under less than 15 DEG C/h less than 200 DEG C；
11) annealing after cleaved, annealing temperature is 750～850 DEG C, and annealing and temperature retention time are not less than 1550min；
12) carrying out cold rolling, cold rolling pass is 1 ~ 3, and total reduction is 15 ~ 30%；
13) quench: control hardening heat is at 850～950 DEG C, and Quenching Soaking Time is not less than 30min；
14) being tempered, control temperature is at 600～700 DEG C, and tempering insulation time is not less than 50min；After tempered
Metallographic structure be tempered martensite；
15) inspection and stand-by.
Table 1 various embodiments of the present invention and compared steel chemical composition (wt%)
Table 2 embodiment of the present invention and the main processes of comparative example
Table 3 embodiment of the present invention and the heat treatment process contrasting steel grade
Note: each embodiment value not one-to-one relationship of table 1 to table 3.
Table 4 embodiment of the present invention and the mechanics assay of comparative example
From table 4, it can be seen that steel grade of the present invention has high intensity (Rm: 1600 ~ 2400MPa), high resiliency, high yield limit
With the highly anti-fatigue limit, there are good cold-rolling workability energy and low-temperature flexibility level (-40 DEG C of KV2>=34J), can be used for manufacturing respectively
Class vehicular clutch assembly, particularly low temperature environment use the large-scale engineering machinery vehicle required.
Above-described embodiment is only and most preferably enumerates, and is not the restriction to embodiments of the present invention.
Claims (1)
1. a kind of method producing high-carbon cold rolled automobile diaphragm spring steel, its step:
1) desulfurizing iron is carried out；
2) converter smelting is carried out；
3) refine in LF stove；
4) process in RH vacuum drying oven, control vacuum processing time no less than 20 minutes；Final steel water component and weight hundred
Proportion by subtraction content is: C:0.72 ~ 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；
5) it is casting continuously to form base: electromagnetic agitation is all the time in casting process；And strand is carried out slighter compress, reduction ratio is 2% ~ 8%；
6) carry out pit slow cooling after strand is cleaved and be cooled to room temperature；
7) heating strand, heating and temperature control is 1200～1300 DEG C, and it is 8～14 minutes/centimetre that the rate of heat addition controls；
8) segmentation hot rolling is carried out: control roughing start rolling temperature, at 1050～1070 DEG C or 1190 ~ 1200 DEG C, controls finish rolling finish to gauge temperature
Degree is at 800～900 DEG C；
9) batch, control coiling temperature at 760～800 DEG C；
10) carrying out slow cooling, cooling velocity controls to be cooled under less than 15 DEG C/h less than 200 DEG C；
11) annealing after cleaved, annealing temperature is 750～850 DEG C, and annealing and temperature retention time are not less than 1550min；
12) carrying out cold rolling, cold rolling pass is 1 ~ 3, and total reduction is 26 ~ 30%；
13) quench: control hardening heat is at 910～950 DEG C, and Quenching Soaking Time is not less than 30min；
14) being tempered, control temperature is at 620～700 DEG C, and tempering insulation time is not less than 50min；Gold after tempered
Phase constitution is tempered martensite；
15) inspection and stand-by.
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| CN107419196B (en) * | 2017-09-18 | 2019-12-20 | 东北大学 | Yield ratio controllable ultralow-carbon easy-to-weld medium manganese steel for automobiles and preparation method thereof |
| KR102010053B1 (en) * | 2017-11-07 | 2019-08-12 | 주식회사 포스코 | High strength and low toughness cold-rolled steel sheet having good fracture characteristics, method for manufacturing same |
| CN108817338B (en) * | 2018-07-06 | 2020-01-24 | 青岛特殊钢铁有限公司 | Continuous casting and rolling production process suitable for high-strength spring flat steel |
| CN114107841B (en) * | 2022-01-27 | 2022-04-12 | 北京科技大学 | High-strength corrosion-resistant spring steel and preparation method thereof |
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| 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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| JP4969907B2 (en) * | 2006-05-15 | 2012-07-04 | 日新製鋼株式会社 | Steel plate for door member and manufacturing method thereof |
| JP5328331B2 (en) * | 2008-12-11 | 2013-10-30 | 日新製鋼株式会社 | Steel materials for wear-resistant quenched and tempered parts and manufacturing method |
| JP5484103B2 (en) * | 2009-02-17 | 2014-05-07 | 日新製鋼株式会社 | Steel plate for high-strength machine parts, method for producing the same, and method for producing high-strength machine parts |
| JP5324311B2 (en) * | 2009-05-15 | 2013-10-23 | 株式会社神戸製鋼所 | Hollow seamless pipe for high strength springs |
| CN102943214B (en) * | 2012-11-16 | 2014-10-08 | 武汉钢铁(集团)公司 | Automotive cold-rolled diaphragm spring steel and production method thereof |
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