CN1082549C - Production of highly resistant, very ductile steel strip - Google Patents

Production of highly resistant, very ductile steel strip Download PDF

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Publication number
CN1082549C
CN1082549C CN988040182A CN98804018A CN1082549C CN 1082549 C CN1082549 C CN 1082549C CN 988040182 A CN988040182 A CN 988040182A CN 98804018 A CN98804018 A CN 98804018A CN 1082549 C CN1082549 C CN 1082549C
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steel
alloying
hot rolled
rolled strip
temperature
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Expired - Fee Related
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CN988040182A
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CN1252105A (en
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B·恩格勒
G·斯迪克
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ThyssenKrupp Steel Europe AG
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ThyssenKrupp Stahl AG
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
    • 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
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/002—Bainite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/008—Martensite

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Heat Treatment Of Steel (AREA)

Abstract

The invention relates to a method for producing a highly resistant (at least 900MPa), very ductile steel strip. The steel, containing (in mass per cent); 0.10 to 0.20 % C; 0.30 to 0.60 % Si; 1.50 to 2.00 % Mn; max. 0.08 % P; 0.30 to 0.80 % Cr; up to 0.40 % Mo; up to 0.20 % Ti and/or Zr; up to 0.08 % Nb; the remainder being Fe and unavoidable impurities, is melted, cast in slabs and then rolled out into a hot rolled strip. The roll end temperature is above 800<o>C, the cooling speed on the delivery roller table is at least 30<o>C/s and the reel temperature is 300 to 600<o>C.

Description

Production has the method for the band steel of high strength and favorable forming property
The present invention relates to produce the method for band steel with the high strength that is at least 900MPa and favorable forming property.
The fuel consumption that reduces vehicle needs the notion of applying light.By reducing the thickness of steel disc, can obtain lightweight member.For compensating the loss of the component strength that causes thus, just must increase the intensity of material.But any increase of intensity all can cause the decline of deformation performance usually.Employed steel sheet must obtain to design upward or desired net shape on the function by the processing that is shaped in the vehicle manufacturing.If the reduction of the increase of intensity and the forming property that causes thus is too many, shaping then is because the local necking down and the appearance of tearing can cause the generation of losing efficacy.For this reason, the increase of intensity is restricted.
The purpose of the development of steel always is to improve the ratio between deformation performance and intensity.
By using the steel of phosphorus alloyization or microalloying, for the situation of the strength range that is lower than 500MPa reduce to have obtained aspect the steel plate thickness quite successful.Use baking hardened steel even can obtain better result.In the strength range between 500-800MPa, dual phase steel and TRIP (phase change induction plasticity) steel has goodish crystallized ability.
Representational eigenwert can obtain from tension test in relevant with plasticity, the actual processing.Especially, unit elongation during fracture and n value (representing the amount of reinforcement ability) are all represented the important dimension index that has.The deformation performance of n value representative under the stretch forming stress.This is the most of steel sheet component main deformational mechanism in the vehicle.The ratio of n value and yielding stress and tensile strength is to deserved fairly good, and this ratio is also represented the reinforcement ability of material in the actual processing.
Reduce the advantage of steel plate thickness for maximally utilising to gain in strength, the unit elongation (A) when rupturing to relating to and the possible maximum of reinforcement value (n value) are inquired into.
Steel with the very high strength that is higher than 800MPa can be used to very effectively reduce and collide the relevant parts such as the impact beam of car door, the weight of baffle plate crossbeam.For this reason, be necessary steel plate thickness from being decreased to more than the 2.0mm below the 2.0mm as 1.5mm.This ultrahigh-strength steel plates can only obtain by cold-rolled steel sheet in the past.
Particularly in being higher than the very high strength scope of 800MPa, when using traditional material notion to produce cold-rolled steel strip or hot rolled strip, deformation performance is not enough to steel plate shaped and is useful parts.Can obtain high strength by forming martensitic stucture.Yet the apparent yielding stress of this steel is also very high.Therefore, the ratio of yielding stress that is obtained and tensile strength and reinforcement value are all lower.Except processability is low, also can cause the elastic recovery value very high, so, the parts of press forming or be difficult to produce, or can not really be shaped.
The objective of the invention is to develop have high-strength voltinism can and the band steel of good crystallized ability and high component strength.
For reaching this purpose, according to the present invention, a kind of method has been proposed, wherein, a kind of steel contains (by percentage to the quality):
The C of 0.10-0.20%
The Si of 0.30-0.60%
The Mn of 1.50-2.00%
Mostly be most 0.08% P
The Cr of 0.30-0.80%
Be no more than 0.40% Mo, preferably be no more than 0.15%
Be no more than 0.20% Ti and/or Zr
Be no more than 0.08% Nb
The Al of 0.025-0.049%
The rest is Fe and unavoidable impurities.
With described steel fusing, pour into steel billet, afterwards, be rolled into hot rolled strip, wherein, finishing temperature is higher than 800 ℃, preferably is higher than 880 ℃, and the speed of cooling on the runoff table is at least 30 ℃/second, and coiling temperature is 300 ℃-600 ℃.
By adjacent soft, hard phase and be distributed with superfine little disperse phase and form very tiny tissue.This tissue that has purpose to set might and use for processing performance attractive, former the unknown is provided.To the heterogeneous sclerosis of tissue, and thin sclerosis brilliant and fine particle constitutes a kind of multiple strengthening mechanism.
Economical characters according to this method of the present invention is that it produces thickness less than 2.0mm, for example the ability of the hot rolled strip of 1.5mm.This production method needn't require as the production of cold-rolled steel strip, needs the additional cold rolling and so complicated production process of annealing operation subsequently.
Material notion of the present invention also comprises the surperficial thinning processing of possibility industrial application.Like this, can carry out such as the electro deposited zinc layer.The zinc layer can obviously improve corrosion resistance nature can think a known fact.And, know that also ultrahigh-strength steel owing to the absorption of hydrogen embrittlement takes place easily in electrolytic process.Can prove that there are not these fearful plating problems in band steel according to the present invention.Therefore, in one aspect of the invention, method of the present invention also comprises carries out cold rolling sclerosis to hot rolled strip.In addition, in the present invention was aspect another, method of the present invention also comprises carried out pickling and metal deposition is handled to steel band, for example adopts metallide, or adopts galvanizing.
Below each alloying element and manufacturing parameter are introduced.
The effect of carbon is to make the hardening of tissue and form ultra-fine disperse phase.Consider welding property, carbon content should be restricted to 0.1-0.2%.
Silicon increases the hardness of sosoloid, thereby requires its content to be at least 0.3%.Consider that from welding property and the formation of avoiding disadvantageous forging scale rudiment its content should be defined as and be no more than 0.6%.
Manganese content was at least 1.5% o'clock, and the carrying out that deferrable changes also causes the formation of hard transmutation product.For avoiding unallowed intensive microsegregation occurring, its content should be defined as and be no more than 2.0%.
Phosphorus can be used to further improve the solution hardening ability, but considers from welding property, and its content should not surpass 0.08%.
Chromium content was at least 0.3% o'clock, can promote to contain the formation of the final tissue of more bainite.For avoiding too postponing the carrying out of transformation, its content should be defined as the highest by 0.80%.
Therefore titanium or zirconium can be used for forming the ultra-fine disperse phase with certain sclerization, wish that its content is too not low, for example can add to be at least 0.04% Ti and/or Zr in steel of the present invention.Yet when its content surpassed 0.2%, this sclerization obviously reduced.Here it is, and why its maximum level must be decided to be 0.2% reason.
Niobium also can be used for dispersion hardening.Its addition preferably is at least 0.04% during alloying.Consider that from validity its content is limited to and is up to 0.08%.
When boron content is 0.0005-0.005%, can improve hardening capacity.So far as is known, this element is used for the martensitic transformation steel.Wonderful discovery, in the present invention, boron also can cause the remarkable increase of bainite base tissue intensity, and the shaping ability just slightly reduces.
Finishing temperature should be in even austenitic area, and should be not less than 800 ℃, to guarantee that the dimensional change drag is enough low and to guarantee that precipitated phase that other deformation brings out seldom.
The reply cooling conditions is selected, avoiding being transformed into perlite, and, make transformation farthest appear at the bainite stage.Martensite in the tissue helps further reinforcement.And, can obtain strengthening effect by separating out also of ultrafine particle.For this purpose, require the cooling at finishing temperature place to carry out with at least 30 ℃/seconds speed of cooling.This process of cooling must finish in the temperature that is lower than 600 ℃, on reeling machine steel band is batched, afterwards, makes steel band continue to cool off at the state that batches again.Therefore, coiling temperature should not be higher than 600 ℃, preferably is not higher than 550 ℃, or is not higher than 350 ℃.Coiling temperature is not less than 300 ℃ in addition, preferably is not less than 330 ℃.In addition, in one aspect of the invention, method of the present invention also comprises after the hot rolling, carries out draught and is at least 30% the continuous annealing of cold rolling and temperature between 700 ℃ and 900 ℃.
Now, present invention is described in conjunction with the following examples.
Table 1 shows band steel 1 produced according to the invention and 2 and the chemical constitution of a kind of martensite contrast steel 3.
Table 2 shows band steel 1 produced according to the invention and 2 and the feature mechanical property of contrast steel 3, and wherein said contrast steel obtains result as shown in table 2 after by the artificial aging of carrying out with postheat treatment.
The comparative result of performance clearly illustrates that band steel produced according to the invention is with the obvious advantage, the unit elongation when it has higher fracture and better as the yielding stress of the reflection of reinforcing degree and the ratio of tensile strength.
Table 3 shows low coiling temperature and thermal treatment subsequently to the band steel Effect on Performance with steel 1 composition in the table 1 produced according to the invention.Coiling temperature preferably is low to moderate 330 ℃, might make the obtainable obvious increase of intensive properties (referring to the embodiment in the table 3 4).
Another purpose of the present invention is to make thermal treatment subsequently play favourable effect.Be surprisingly found out that, by in 500 ℃-850 ℃ temperature range, band steel produced according to the invention heat-treated, even can further improve forming property.
Embodiment 4,5 and 6 in the table 3 shows this thermal treatment to having the influence of the steel of forming shown in the table 11.The state that material reached helps obtaining to require generally good crystallized ability, requires high strength, the member of especially high apparent yielding stress simultaneously again.This performance combination can be used to produce the cold rolled shape (embodiment 5a) with high energy absorption capability.By selecting higher annealing temperature, might obtain high strength, the ratio of especially low yielding stress and tensile strength, and the height under the similarly favourable extensibility is strengthened ability (embodiment 5b, 6a-6c).
The shortcoming of many hot-rolled products is: in case cold rolling and recrystallization annealing processing with it subsequently, the advantageous property of hot-rolled product will be lost.Yet, find that for band steel according to the present invention, after cold rolling and annealing subsequently, it still has favourable performance.The result, embodiment 7 in the table 3 shows, and only compares with 2 through hot rolled band steel 1, and band steel 1 produced according to the invention is after being 50% cold-rolling treatment through deflection, obtaining the high-intensity while, even the ratio that also has the yielding stress and the tensile strength of further improvement.
Table 1
((quality %) by percentage to the quality)
Steel C Si Mn P S Al N Cr Mo Ti
1 0.14 0.47 1.83 0.007 0.002 0.025 0.004 0.34 0.12 0.15
2a 0.19 0.43 1.67 0.013 0.007 0.032 0.007 0.49 0.30 0.18
2b 0.17 0.53 1.82 0.013 0.012 0.049 0.012 0.77 0.02 0.18
3* 0.15 0.01 1.75 0.011 0.003 0.020 0.004 0.55 0.01 0.003
*) martensite contrast steel
Table 2
Steel The position of sample Re N/mm 2 Rm N/mm 2 Re/R m Ag ％ A 5％ A 80％ WET ℃ HT ℃
1 Portraitlandscape 653 652 1065 1098 0.61 0.59 8 8 18 17 11 12 910 530
2a Vertically 670 1115 0.60 7 16 10 880 550
2b Vertically 680 1140 0.60 7 15 9 880 550
3* Vertically 1050 1096 0.96 2 10 5 880 280
*) the unit elongation A of contrast steel Re yield-point Rm ultimate tensile strength Ag homogeneous deformation 5Unit elongation A during fracture 80Unit elongation WET finishing temperature HT coiling temperature during fracture
Table 3
Embodiment Annealing ℃ minute Re N/mm 2 Rm N/mm 2 Re/Rm A 80 ％ WET ℃ HT ℃
4 ./. ./. 1203 1395 0.86 3 910 330
5a 5b 6a 6b 6c 7*a 7*b 600 120 1040 1070 0.97 9 910 330
750 1 690 1190 0.58 7 910 330
750 1 620 1095 0.58 6 910 530
800 1 600 1086 0.55 10 910 530
850 1 492 913 0.54 14 910 530
800 1 627 1149 0.55 8 910 530
850 1 446 959 0.47 12 910 530
*) through draught be 50% cold-rolling treatment

Claims (30)

1. produce have the high strength that is at least 900MPa and excellent formability can the method for band steel, described band steel contains (by percentage to the quality):
The C of 0.10-0.20%
The Si of 0.30-0.60%
The Mn of 1.50-2.00%
Mostly be most 0.08% P
The Cr of 0.30-0.80%
Be no more than 0.40% Mo
Be no more than 0.20% Ti and/or Zr
Be no more than 0.08% Nb
The Al of 0.025-0.049%
The rest is Fe and unavoidable impurities,
With described steel fusing, pour into steel billet, afterwards, be rolled into hot rolled strip, wherein, finishing temperature is higher than 880 ℃, and the speed of cooling on the runoff table is at least 30 ℃/second, and coiling temperature is 300 ℃-600 ℃.
2. the method for claim 1 is characterized in that described hot rolled strip batches in the temperature that is not higher than 550 ℃.
3. the method for claim 1 is characterized in that described hot rolled strip batches in the temperature that is not higher than 350 ℃.
4. one kind as each described method among the claim 1-3, it is characterized in that the coiling temperature of described hot rolled strip is not less than 330 ℃.
5. one kind as each described method among the claim 1-3, it is characterized in that the final rolling thickness of described hot rolled strip is not more than 2.0mm.
6. a method as claimed in claim 4 is characterized in that the final rolling thickness of described hot rolled strip is not more than 2.0mm.
7. one kind as each described method among the claim 1-3, it is characterized in that described hot rolled strip is carried out cold rolling sclerosis.
8. a method as claimed in claim 4 is characterized in that described hot rolled strip is carried out cold rolling sclerosis.
9. a method as claimed in claim 5 is characterized in that described hot rolled strip is carried out cold rolling sclerosis.
10. one kind as each described method among the claim 1-3, it is characterized in that described steel band handles through pickling and metal deposition.
11. a method as claimed in claim 10 is characterized in that described metal deposition adopts electrolytic process to carry out.
12. a method as claimed in claim 10 is characterized in that described metal deposition adopts galvanizing to carry out.
13. one kind as each described method among the claim 1-3, it is characterized in that described hot rolled strip anneals between 500-850 ℃.
14. a method as claimed in claim 4 is characterized in that described hot rolled strip anneals between 500-850 ℃.
15. a method as claimed in claim 5 is characterized in that described hot rolled strip anneals between 500-850 ℃.
16. one kind as each described method among the claim 1-3, it is characterized in that: after the hot rolling, carry out draught and be at least 30% the continuous annealing of cold rolling and temperature between 700 ℃ and 900 ℃.
17. a method as claimed in claim 4 is characterized in that: after the hot rolling, carry out draught and be at least 30% the continuous annealing of cold rolling and temperature between 700 ℃ and 900 ℃.
18. a method as claimed in claim 5 is characterized in that: after the hot rolling, carry out draught and be at least 30% the continuous annealing of cold rolling and temperature between 700 ℃ and 900 ℃.
19. one kind as each described method among the claim 1-3, when it is characterized in that alloying, adds being no more than 0.15% Mo in described steel.
20. a method as claimed in claim 4 when it is characterized in that alloying, adds being no more than 0.15% Mo in described steel.
21. a method as claimed in claim 5 when it is characterized in that alloying, adds being no more than 0.15% Mo in described steel.
22. one kind as each described method among the claim 1-3, when it is characterized in that alloying, adds being at least 0.04% Ti and/or Zr in described steel.
23. a method as claimed in claim 4, when it is characterized in that alloying, interpolation is at least 0.04% Ti and/or Zr in described steel.
24. a method as claimed in claim 5, when it is characterized in that alloying, interpolation is at least 0.04% Ti and/or Zr in described steel.
25. one kind as each described method among the claim 1-3, it is characterized in that: during alloying, in described steel, add the B of 0.0005-0.005%.
26. a method as claimed in claim 4 is characterized in that: during alloying, in described steel, add the B of 0.0005-0.005%.
27. a method as claimed in claim 5 is characterized in that: during alloying, in described steel, add the B of 0.0005-0.005%.
28. one kind as each described method among the claim 1-3, when it is characterized in that alloying, adds being at least 0.04% Nb in described steel.
29. a method as claimed in claim 4, when it is characterized in that alloying, interpolation is at least 0.04% Nb in described steel.
30. a method as claimed in claim 4, when it is characterized in that alloying, interpolation is at least 0.04% Nb in described steel.
CN988040182A 1997-03-13 1998-03-10 Production of highly resistant, very ductile steel strip Expired - Fee Related CN1082549C (en)

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DE19710125.9 1997-03-13
DE19710125A DE19710125A1 (en) 1997-03-13 1997-03-13 Process for the production of a steel strip with high strength and good formability

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AR (1) AR010130A1 (en)
AT (1) ATE206472T1 (en)
CA (1) CA2284124A1 (en)
CZ (1) CZ290944B6 (en)
DE (2) DE19710125A1 (en)
ES (1) ES2165157T3 (en)
PL (1) PL186831B1 (en)
WO (1) WO1998040522A1 (en)
ZA (1) ZA982115B (en)

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CA2284124A1 (en) 1998-09-17
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EP0966547A1 (en) 1999-12-29
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DE59801637D1 (en) 2001-11-08
EP0966547B1 (en) 2001-10-04

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