CN1051764A - The high tensile strength cold-rolled steel sheet of stretching flanging characteristic good and hot-dip galvanized steel sheet and manufacture method thereof - Google Patents
The high tensile strength cold-rolled steel sheet of stretching flanging characteristic good and hot-dip galvanized steel sheet and manufacture method thereof Download PDFInfo
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Abstract
The present invention relates to tensile strength is 40kgf/mm
2More than, and ductility, the cold-rolled steel sheet of the flanging characteristic good that particularly stretches, hot-dip galvanized steel sheet and their manufacture method.Because the present invention used fine and uniform ferritic phase suitably, thereby cold-rolled steel sheet of the present invention and hot-dip galvanized steel sheet be the material that can keep enough intensity and have high yield ratio after forming process, can be used as the strength member that automobile is used.
Description
The present invention relates to tensile strength (following represent) and be 40kgf/mm with T.S.
2More than, and ductility, good cold-rolled steel sheet, the hot-dip galvanized steel sheet of the flanging characteristic that particularly stretches (stretching び Off ラ Application ジ characteristic), and their manufacture method.
T.S. surpass 40kgf/mm
2High tensile strength cold-rolled steel sheet, for example in automotive industry in order to improve security, to reduce fuel cost with lightweight, and strengthen antirust, and higher to the requirement of the hot-dip galvanized steel sheet that uses high tensile strength cold-rolled steel sheet.In addition, in the building materials purposes, wish that the material of construction thin-walled property to reduce cost, therefore also has very high requirement to high tensile strength cold-rolled steel sheet.
This high-tensile steel in above-mentioned all purposes, self-evidently also should satisfy processibilities such as desirable press working.
Attempt to satisfy the technology of these requirements, having the spy to open clear 57-63634 number and 56-13437 communique disclosed is the manufacture method of former material with the Mn-Si steel, but this method mainly is to handle by solution strengthening to make it high tensileization, want heavy addition to help the Si of high strength, thereby causing surface properties, chemical conversion and plating aspect all have problems.
Other is not as depending on the method for alloying constituent, opens according to as described in the 60-33318 communique as the spy, utilizes the method for recovering annealed structure, but the material instability is arranged, ductility is low, and the problem of aspect such as intra-face anisotropy is big, so that can not low-cost a large amount of the manufacturing.
The present invention relates to a kind of T.S. and surpass 40kgf/mm
2High tensile strength cold-rolled steel sheet and high tensile hot-dip galvanized steel sheet, its objective is to solving the problem that prior art exists, a kind of high tensile strength cold-rolled steel sheet, high tensile hot-dip galvanized steel sheet and their manufacture method that can reach the stretching flanging excellent of following condition is provided.
(1) can avoid making surface properties to worsen and the deleterious Si of plating is added, and be low-alloy system.
(2) improve ductility, the flanging characteristic particularly stretches.
(3) can obtain the few stable material of intra-face anisotropy.
(4) operational condition that needn't the special stipulation strictness.
Present inventors are for addressing the above problem, the steel and various its material and the tissue of creating conditions down of the various composition of comprehensive survey system, investigation result is found, the branch rate of perlite grade in an imperial examination 2 phases is reduced, as the recrystallize ferritic structure, and can obtain extremely excellent stretching flanging characteristic when making its tissue become even subparticle, and then find that the tissue of this hope mainly is to obtain by composition and cold rolling condition annealing conditions best of breed with steel.
The present invention is with the above-mentioned basis that is found to be.
Be that the present invention is a kind of high tensile strength cold-rolled steel sheet of the flanging excellent that stretches, its composition is to contain below C:0.03～0.15wt%(simply to represent with %), below the Si:0.05%, Mn:0.5～1.2%, Nb:0.005～0.045% and below the Al:0.10%, surplus is that iron and unavoidable impurities are formed, and has the tissue that 20 μ m following even fine recrystallize ferrite in average crystal grain footpath accounts for 95% above area.
The invention still further relates to the manufacture method of the high tensile strength cold-rolled steel sheet of stretching flanging excellent.It is characterized in that, to contain C:0.03～0.15%, below the Si:0.05%, Mn:0.5～1.2%, Nb:0.005～0.045% and below the Al:0.10%, surplus is that the steel that constituted of iron and unavoidable impurities is as former material, after this former material carried out hot rolling, carry out cold rollingly, heating with the rate of heating more than 5 ℃/second on the continuous annealing line subsequently to surpass 50% draft, keep annealing in 20～60 seconds 720 ℃～780 ℃ temperature ranges, cool off then.
The invention still further relates to a kind of high tensile hot-dip galvanized steel sheet of the flanging excellent that stretches, its consist of contain C:0.03～0.15%, below the Si:0.05%, Mn:0.5～1.2%, Nb:0.005～0.045% and below the Al:0.10%, surplus is constituted by iron and unavoidable impurities, and has the tissue that 20 μ m following even fine recrystallize ferrite in average crystal grain footpath accounts for 95% above area.
The invention still further relates to the manufacture method of the high tensile fused zinc steel plate of stretching flanging excellent, it is characterized in that, to contain C:0.03～0.15%, below the Si:0.05%, Mn:0.5～1.2%, Nb:0.005～0.045% and below the Al:0.10%, surplus is that the steel that constituted of iron and inevitable impurity is as former material, after this former material carried out hot rolling, carry out cold rolling with draft above 50%, heat with the rate of heating more than 5 ℃/second on the continuous fusion galvanizing line of annealing way in online subsequently, in 720 ℃～780 ℃ temperature range, keep annealing in 20～60 seconds, treat then to carry out the plating processing after its cooling.
The invention still further relates to the manufacture method of the high tensile hot-dip galvanized steel sheet of stretching flanging excellent, it is characterized in that, to contain C:0.03～0.15%, below the Si:0.05%, Mn:0.5～1.2%, Nb:0.005～0.045% and below the Al:0.10%, surplus is that the steel that constituted of iron and inevitable impurity is as former material, after this former material carried out hot rolling, carry out cold rolling with draft above 50%, heat with the rate of heating more than 5 ℃/second on the continuous fusion galvanizing line of annealing way in online subsequently, in 720 ℃～780 ℃ temperature range, keep annealing in 20～60 seconds, treat then to carry out the plating processing after its cooling, carry out Alloying Treatment subsequently.
At first illustrate steel plate of the present invention, one-tenth is grouped into the reason that is limited in the above-mentioned scope.
C：0.03～0.15%
C is the most effective as strengthening composition, and price low therefore be the composition of wishing, significantly increase but addition surpasses minute rate of the 2nd phase of 0.15% o'clock perlite etc., the ductility flanging that particularly stretches significantly worsens, weldability also significantly worsens.On the other hand, during the addition less than 0.03% of C, also can not get enough T.S, therefore, be decided to be 0.03～0.15% scope even add other composition.
Below the Si:0.05%
Si is effective to the reinforcement of steel, and it is very little to the deleterious effects of ductility, therefore see it is the composition of wishing heavy addition from mechanical properties, but, Scaling significantly worsens owing to making surface properties, and be unfavorable for plating, therefore in order to obtain beautiful surface, its content must be below 0.05%.
Mn：0.5～1.2%
Mn is the efficient hardening composition that its solution strengthening can not can influence C, Si etc.Mn also has the perlite of inhibition and excessively generates and thickization, makes the effect of crystal grain miniaturization.In order to bring into play these effects, the addition of Mn must be more than 0.5%.On the other hand, if Mn amount surpasses 1.2%, then strengthening effect is tending towards saturated, and the 2nd tendency that demonstrates layered distribution mutually, therefore, the deterioration of stretching flanging, plating also worsens.Therefore deciding its scope is 0.5～1.2%.
Nb：0.005～0.045%
The interpolation of Nb and the control of addition are important factors of the present invention.Among the present invention, the additive effect of Nb finally can obtain trickle and uniform recrystallize ferritic structure, so that improves intensity and the ductility flanging characteristic that particularly stretches.Think that Nb may fold as carbonitride, bring above-mentioned desirable effect, but its detailed mechanism is not clear.This ideal effect can only surpass 0.005% and just can obtain at the addition of Nb.And surpassing 0.045%, its effect is saturated, is uneconomic therefore.And excessive interpolation can cause being difficult to stably make steel.Therefore, its scope is decided to be 0.005～0.045%.
Below the Al:0.10%
Al: it is integral added ingredients as the deoxidation composition and for the purification of steel.Therefore Al preferably adds 0.005% at least.But, surpassing at 0.10% o'clock, generation aluminum oxide slag etc. causes the dangerous high of surface imperfection, therefore fixes on below 0.10%.
Except that mentioned component, as the unavoidable impurities composition, allow that N, O and S reach 0.0050%, 0.0070% and 0.010% respectively among the present invention.Particularly S makes its reduction can significantly improve stretching flanging characteristic.So just can reach makes T.S. surpass 45kgf/mm
2More high strength.Therefore, if want to reach high strength, it is favourable reducing S.
The qualification reason of crystal structure below is described.
Purpose of the present invention is to improve ductility as mentioned above, and the flanging characteristic especially stretches.
This specific character is that the branch rate with the 2nd phase of perlite etc. reduces, and making recrystallize ferrite branch rate is more than 95%, and can obtain extremely excellent stretching flanging characteristic when making its tissue become the following even particulate of average 20 μ m.
At this moment, the branch rate of perlite (thick especially) that becomes stretching flanging crackle starting point is many more unfavorable more, and if the recrystallize ferritic structure is inhomogeneous and thick unfavorable equally, this is undesirable, therefore, dividing calibration with the recrystallize ferrite is more than 95%, and the ferritic average crystallite particle diameter of recrystallize is decided to be below the 20 μ m.
Below narrate the qualification reason of creating conditions.
Have no particular limits to the hot rolled operation by the system steel, can make according to normally used method.As representational hot-rolled condition, can exemplify: 1280～1180 ℃ of Heating temperatures, 900～800 ℃ of hot rolling processing temperatures, 650～500 ℃ of coiling temperature.
As for cold rolling, in general its draft is high then helps the granular of organizing after the recrystallization annealing, and in view of this consideration, the following of cold rolling draft is defined as 50%.But, cold rolling draft is brought up to essential value when above, though to material and the harmless problem that can bring hot rolling motherboard thickness to increase.
About annealing heating rate in the continuous fusion galvanizing line of annealing way in the line of the continuous annealing line of cold-rolled steel sheet and hot-dip galvanized steel sheet, it is fast favourable to recrystallize grain granular, in order to obtain even and trickle recrystallize grain, be necessary it is defined in more than 5 ℃/second, wish more than 10 ℃/second.And the upper limit of rate of heating, in view of the setting of heating installation, the consideration of technology and economic aspects is decided to be 100 ℃/second.
Annealing temperature is decided to be 720～780 ℃.Be lower than 720 ℃ low temperature then recrystallize can not fully carry out, extensibility reduces, the stretching flanging also reduces, and therefore can not get satisfied material.If but surpassed 780 ℃ then can produce softening because of crystal grain-growth, this would be undesirable.Among the present invention, owing to add Nb, the carbonitride of Nb suppresses the misgrowth of recrystallize grain, therefore can obtain trickle recrystallize ferrite crystal grain tissue in wide temperature range.
In fact this annealed hold-time does not have good, but considers the stability of material, and the hold-time was favourable more than 20 seconds.Cause the material deterioration if surpass 60 seconds then might grow up, therefore be decided to be 20-60 second because of abnormal grain.
In the purposes of the present invention's steel plate, as the intensity after the forming process of parts, the yielding stress of raw sheet is most important, even therefore often wishing a little sacrifices formability and will guarantee that also yield ratio (Y.R.) is more than 70%, in order to obtain this high strength and suitable yield ratio, in being right after the annealed process of cooling, preferably at least 700～500 ℃ temperature range, carry out speed of cooling and be the chilling more than 20 ℃/second.
During hot-dip galvanized steel sheet is made, the plating after the annealing is handled, there is no particular limitation, handles just with common method plating.And, pay no attention among the present invention and have or not Alloying Treatment.The characteristic variations that this Alloying Treatment causes is very little, becomes identical material in fact.
Embodiment
Embodiment 1
Make the steel billet that the various one-tenth shown in the table 1 are grouped into according to usual way.
Table 1
These steel billets are carried out hot rolling under condition shown in the table 2, cold rolling, in continuous annealing line, anneal subsequently.
To the steel plate that obtains thus, measure corresponding to the anti-characteristic of opening of steel plate, the lateral bending song of stretching flanging characteristic (サ ィ De ベ Application De) tensile properties, evaluation result is shown in table 3, tension test No. 5 test film evaluations of JIS.About the bent tensile properties of lateral bending, estimate according to the public clear 50-35438 communique disclosed method of spy, with wide 40mm, the strip test film of long 170mm, consider to have suitable space whenever blocking when particularly making, and process truncation surface for test with sand paper lightly, and make the in-plane bending distortion, estimate the pulled out condition at flanging position when crackle takes place.
Table 3
Bent the 2nd phase average ferrite summary of steel Y.S. T.S. EL. Y.R. lateral bending
Kgf/mm
2Kgf/mm
2The branch rate % crystallization particle diameter μ m of % % stretching %
A 40 46 37 87＞60 3 14 embodiment
B 39 47 37 83＞60 4 14 embodiment
C 40 48 35 83＞60 2 12 embodiment
D 34 36 35 94 58＜1 26 comparative examples
E 36 49 32 73 45 8 13 comparative examples
F 42 43 25 98 45 3 25 comparative examples
G 38 45 33 84 50 2 11 comparative examples
H 39 43 30 91 48 2 12 comparative examples
I 34 38 25 89 60 7 25 comparative examples
J 39 47 37 83＞60 2 13 embodiment
K 39 49 37 80＞60 4 14 embodiment
L 39 48 37 81＞60 3 14 embodiment
M 41 50 35 82＞60 3 14 embodiment
N 41 47 37 87＞60 3 14 embodiment
O 42 50 35 84＞60 2 13 embodiment
P 42 49 35 86＞60 2 12 embodiment
As seen from Table 3, if the present invention's composition compositing range, although be high strength (T.S. 〉=40kgf/mm
2), also can obtain good stretching (El.) and lateral bending Qu Lashen, the flanging characteristic promptly stretches.And can obtain suitable yield ratio.
Embodiment 2
Employing has the steel that table 1 becomes to be grouped into, and is making cold-rolled steel sheet under the various conditions shown in the table 4, and is identical with embodiment 1, and anti-characteristic and the bent tensile properties of lateral bending opened of investigation the results are shown in table 5.
Table 4
The cold rolling draft rate of heating of steel annealing temperature annealing time speed of cooling summary
(%) (℃/second) (℃) (second) (℃/second)
1 60 12 740 20 25 embodiment
2 70 10 730 40 27 embodiment
3 45 10 740 20 30 comparative examples
4 60 3 740 40 22 comparative examples
5 60 20 760 20 32 embodiment
6 60 12 700 40 28 comparative examples
7 60 12 800 40 30 comparative examples
8 55 15 725 5 25 comparative examples
9 50 15 725 40 30 embodiment
10 60 5 740 30 30 embodiment
11 60 12 780 30 25 embodiment
12 55 10 720 40 25 embodiment
13 60 10 725 60 20 embodiment
Table 5
The average ferrite of bent the 2nd phase of steel Y.S. T.S. T.R. El. lateral bending
Kgf/mm
2Kgf/mm
2% % stretching % divides rate % crystallization particle diameter μ m
1 39 47 83 38 ＞60 1.8 19
2 38 46 83 39 ＞60 1.7 17
3 66 71 93 9 20 2.1 24
4 38 40 95 38 ＞60 3.2 23
5 39 47 83 36 ＞60 2.1 19
6 55 65 85 12 28 1.8 a part of non-recrystallizations
7 33 35 94 35 ＞60 3.1 22
8 49 56 87 19 30 3 a part of non-recrystallizations
9 37 46 80 38 ＞60 2.2 17
10 40 48 83 38 ＞60 1.7 17
11 37 46 80 38 ＞60 1.5 17
12 40 49 81 37 ＞60 2.2 17
13 39 46 85 38 ＞60 1.5 17
Be clear that by table 5,, can obtain good intensity one and stretch and take into account and stretch the flanging characteristic if in the present invention's the scope of creating conditions.
Embodiment 3
For the influence of survey organization to ductility, stretching flanging characteristic, composition shown in the employing table 6 and the steel that are for experiment of creating conditions down and making change and form and treatment condition, investigate their corresponding relation, the results are shown in table 7.
As seen from Table 7, by the branch rate of suitable control the 2nd phase, recrystallize ferrite median size, recrystallize ferrite area occupation ratio then can obtain good material.In the Comparative Examples, 5 T.S. is at 40kgf/mm
2Below, stretch, the bent tensile properties of lateral bending is good, but the ferrite median size surpasses 20 μ m, the satisfied material of can not saying so.
Table 7
Steel the 2nd phase and ferrite median size recrystallize ferrite E1. lateral bending Qu Lashen
Its minute rate (%) (μ m) area occupation ratio (%) % (%)
1 perlite＜2% 14 98 38＞60
2 the same 17～100 38＞60
3 the same 18 90 30 31
4 perlite 7% 14 93 32 36
5 perlite 6% 23 94 33＞60
Embodiment 4
Make the steel billet that various one-tenth are grouped into shown in the table 1 according to usual method.These steel billets are carried out hot rolling, cold rolling under condition shown in the table 8, anneal on the continuous fusion galvanizing line of online subsequently interior annealing way, then carry out plating processing, Alloying Treatment, thereby make alloy galvanized steel plate.
To the steel plate that makes thus, measure the bent tensile properties of its lateral bending corresponding to tensile properties, stretching flanging characteristic, table 9 illustrates its evaluation result.Tension test is with JIS No. 5 test films, also is offside bend tension characteristic, carries out the same evaluation of embodiment 1.
Table 9
Steel Y.S. T.S. Y.R. El. lateral bending other the 2nd on average the summary
Kgf/mm
2Kgf/mm
2% % song draws the iron element of phase
Stretch % branch rate % body grain
Footpath μ m
A 39 45 87 38＞60 3 15 embodiment
B 38 46 83 37＞60 4 17 embodiment
C 40 48 83 34＞60 2 15 embodiment
D 33 35 94 35 57＜1 28 comparative examples
E 35 48 73 33 44 9 13 comparative examples
F 41 42 98 25 44 3 26 comparative examples
G 38 45 84 34 51 2 12 comparative examples
H does not plate 3 12 comparative examples in 39 43 91 29 49 many places
I 34 38 89 24 59 7 25 comparative examples
J 38 45 84 36＞60 5 12 embodiment
K 38 47 81 37＞60 4 15 embodiment
L 38 46 83 37＞60 4 15 embodiment
M 40 48 83 36＞60 4 13 embodiment
N 40 46 87 37＞60 2 14 embodiment
O 41 48 85 34＞60 3 12 embodiment
P 41 48 85 36＞60 3 13 embodiment
Can be clear that by table 9, if the present invention's composition compositing range, although be high strength (T.S. 〉=40kgf/mm
2), also can obtain good stretching (El.) and lateral bending Qu Lashen, the flanging characteristic promptly stretches.
Embodiment 5
Employing has the A steel that table 1 becomes to be grouped into, under each condition shown in the table 10, and the hot-dip galvanized steel sheet of alloying hot-dip galvanized steel sheet and non-alloying, identical with embodiment 1, the bent tensile properties of investigation tensile properties and lateral bending the results are shown in table 11.
Table 10
Cold rolling rate of heating annealing annealing speed of cooling has the alloy-free summary
Following rate (%) (℃/second) temperature-time (℃/second) is changed processing
(℃) (second)
1 60 12 740 20 30 have or not embodiment
2 70 10 730 40 30 have embodiment
3 45 10 740 20 35 have comparative example
4 60 3 740 40 20 have comparative example
5 60 20 760 20 30 have or not embodiment
6 60 12 700 40 29 have comparative example
7 60 12 800 40 30 have comparative example
8 55 15 725 5 27 have comparative example
9 50 15 725 40 30 have embodiment
10 60 5 740 30 30 have embodiment
11 60 12 780 30 25 have embodiment
12 55 10 720 40 20 have embodiment
13 60 10 725 60 25 have embodiment
Table 11
The average ferrite of bent the 2nd phase of steel Y.S. T.S. Y.R. El. lateral bending
Kgf/mm
2Kgf/mm
2% % stretching % divides rate % crystallization particle diameter μ m
1 38 46 83 39 ＞60 1.5 18
2 38 46 83 38 ＞60 1.5 17
3 65 70 93 8 20 2 25
4 38 40 95 39 ＞60 3 23
5 39 47 83 37 ＞60 2 18
6 55 65 85 12 28 1.5 a part of non-recrystallizations
7 33 35 94 36 ＞60 3 22
8 48 55 87 18 30 3 a part of non-recrystallizations
9 37 46 80 37 ＞60 2.0 18
10 38 46 83 38 ＞60 1.5 17
11 37 46 80 39 ＞60 1.5 18
12 38 47 81 38 ＞60 2.0 17
13 39 46 85 38 ＞60 1.5 17
Can be clear that by table 11,, then can obtain good intensity-stretching flanging characteristic of taking into account and stretch if in the scope of creating conditions of the present invention.Have or not Alloying Treatment very little, become identical material in fact the influence of material.
Embodiment 6
For survey organization to ductility, the influence of stretching flanging characteristic, composition shown in the employing table 12 and the steel that are for experiment of creating conditions down and making change to be formed and treatment condition, investigate their corresponding relation, the results are shown in table 13.
As seen from Table 13, separation, recrystallize ferrite median size and recrystallize ferrite area occupation ratio by suitable control the 2nd phase then can obtain good material.In the Comparative Examples, 5 T.S. is at 40kgf/mm
2Below, stretching, the bent tensile properties of lateral bending is good, but the ferrite grain is through surpassing 20 μ m, the satisfied material of can not saying so.
Table 13
Steel the 2nd phase and ferrite median size recrystallize ferrite El. lateral bending Qu Lashen
Its minute rate (%) (μ m) area occupation ratio (%) % (%)
1 perlite＜2% 15 98 39＞60
2 the same 18～100 37＞60
3 the same 18 90 31 30
4 perlite 8% 15 92 31 35
5 perlite 7% 25 93 34＞60
Embodiment 7
Adopt the steel of the system of composition shown in the table 14, carry out the hot rolling processing temperature and be 800～850 ℃ hot rolling and cold rolling draft and be 65% cold rolling after, heat and impose 740 ℃ of equal thermal annealings of following 30 seconds with 10 ℃/second, then after carrying out plating processing and further Alloying Treatment, according to embodiment 1 method investigation stretching flanging characteristic.
Table 14
Chemical ingredients (%)
Steel C Si Mn Nb Al N O S
Q 0.07 0.02 0.85 0.010 0.025 0.020 0.010 0.010
R 0.08 0.02 0.80 0.012 0.035 0.025 0.015 0.007
S 0.07 0.01 0.75 0.010 0.020 0.025 0.010 0.005
T 0.07 0.02 0.75 0.012 0.025 0.025 0.010 0.003
U 0.08 0.01 0.85 0.012 0.025 0.025 0.010 0.001
In this test, its condition should be stricter than embodiment 1, and the gap when blocking is bigger than common, and do not carry out end face fully and handle for test, and it the results are shown in table 15.
Table 15
Steel lateral bending Qu Lashen
Q 55%
R 57%
S ＞60%
T ＞60%
U ＞60%
In the table 15, the lateral bending song of steel Q is stretched as 55%, and this value is more much better than former steel, then can further improve this characteristic but further reduce S.In the table 15,＞60% expression test film pushes through the crackle state does not take place between anchor clamps, and expression has the bent tensile properties (stretching flanging characteristic) of extremely excellent lateral bending.
The present invention relates to the high tensile strength cold-rolled steel sheet of a kind of with in the past different high strength and ductility, stretching flanging excellence, and dissolve steel plate galvanized.In the past, be 40kgf/mm as T.S.
2Above high-tensile steel, most because of shortcoming stretching flanging cracks, and be difficult to obtain as parts such as automobile, to require the material that can keep enough intensity and have high yield ratio after the forming process.And when hot-dip galvanized steel sheet carries out surface treatment, become the obstacle of high strength and plating etc.And the present invention has been owing to used trickle and uniform ferritic phase suitably, thereby solved this problem.Mainly can be used as the Rustproof Steel Plate of automobile with strength member.
Claims (5)
1, a kind of high tensile strength cold-rolled steel sheet of the flanging excellent that stretches is characterized in that it contains:
C：0.03～0.15wt%，
Below the Si:0.05wt%,
Mn：0.5～1.2wt%，
Nb：0.005～0.045wt%，
Below the Al:0.10wt%,
And surplus is made of iron and unavoidable impurities, and to have the average crystallite particle diameter be that the area occupation ratio of the following even trickle recrystallize ferritic structure of 20 μ m is the tissue more than 95%.
2, a kind of manufacture method of high tensile strength cold-rolled steel sheet of the flanging excellent that stretches is characterized in that, will contain
C：0.03～0.15wt%，
Si：0.05wt%，
Mn：0.5～1.2wt%，
Nb：0.005～0.045wt%，
Below the Al:0.10wt%,
And the steel that surplus is made of iron and inevitable impurity is as former material,
After this former material carried out hot rolling,
Carry out draft and be cold rolling more than 50%,
Then heating with the rate of heating more than 5 ℃/second on the continuous annealing line and in 720 ℃～780 ℃ temperature range, keeping annealing in 20～60 seconds, cool off then.
3, a kind of high tensile hot-dip galvanized steel sheet of the flanging excellent that stretches, it is characterized in that: it contains:
C：0.03～0.15wt%，
Below the Si:0.05wt%,
Mn：0.5～1.2wt%，
Nb：0.005～0.045wt%，
Below the Al:0.10wt%,
And surplus is made of iron and unavoidable impurities,
And having the average crystallite particle diameter is that the plain area occupation ratio of organizing of the following even trickle recrystallize iron of 20 μ m is the tissue more than 95%.
4, a kind of high tensile hot-dip galvanized steel sheet manufacture method of the flanging excellent that stretches is characterized in that, will contain
C：0.03～0.15wt%，
Si：0.05wt%，
Mn：0.5～1.2wt%，
Nb：0.005～0.045wt%，
Below the Al:0.10wt%,
And the steel that surplus is made of iron and inevitable impurity is as former material,
After this former material carried out hot rolling,
Carry out draft and be cold rolling more than 50%,
Then in online on the continuous fusion galvanizing line of annealing way with the heating of the rate of heating more than 5 ℃/second and in 720 ℃～780 ℃ temperature range, keep annealing in 20～60 seconds, after its cooling, impose plating and handle.
5, a kind of high tensile hot-dip galvanized steel sheet manufacture method of the flanging excellent that stretches is characterized in that, will contain
C：0.03～0.15wt%，
Below the Si:0.05wt%,
Mn：0.5～1.2wt%，
Nb：0.005～0.045wt%，
Below the Al:0.10wt%,
And the steel that surplus is made of iron and inevitable impurity is as former material,
After this former material carried out hot rolling,
Carry out draft and be cold rolling more than 50%,
Then heat with the rate of heating more than 5 ℃/second on the continuous fusion galvanizing line of annealing way in online, and in 720 ℃～780 ℃ temperature range, keep 20-60 to anneal second, after its cooling, impose plating and handle and later Alloying Treatment.
Applications Claiming Priority (5)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP29615889 | 1989-11-16 | ||
| JP296158/89 | 1989-11-16 | ||
| JP88122/90 | 1990-04-04 | ||
| JP276471/90 | 1990-10-17 | ||
| JP2276471A JP2688384B2 (en) | 1989-11-16 | 1990-10-17 | High-strength cold-rolled steel sheet and hot-dip galvanized steel sheet having excellent stretch flange characteristics, and methods for producing the same |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN1051764A true CN1051764A (en) | 1991-05-29 |
| CN1025224C CN1025224C (en) | 1994-06-29 |
Family
ID=26551918
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN 90109291 Expired - Fee Related CN1025224C (en) | 1989-11-16 | 1990-11-16 | Cold-rolled high tonsion steel strip having excellent stretching and folding properties, and molten zinc coating steel strip, and process for manufacturing same |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN1025224C (en) |
Cited By (10)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN100408711C (en) * | 2002-06-25 | 2008-08-06 | 杰富意钢铁株式会社 | High-strength cold rolled steel sheet and process for producing the same |
| CN102094149A (en) * | 2011-03-08 | 2011-06-15 | 攀钢集团钢铁钒钛股份有限公司 | Niobium-containing high-strength hot-galvanized steel plate and production method thereof |
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| CN107406947A (en) * | 2015-03-25 | 2017-11-28 | 杰富意钢铁株式会社 | High-strength steel sheet and its manufacture method |
| CN107429355A (en) * | 2015-03-25 | 2017-12-01 | 杰富意钢铁株式会社 | High-strength steel sheet and its manufacture method |
| CN107923013A (en) * | 2015-08-19 | 2018-04-17 | 杰富意钢铁株式会社 | High-strength steel sheet and its manufacture method |
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1990
- 1990-11-16 CN CN 90109291 patent/CN1025224C/en not_active Expired - Fee Related
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|---|---|---|---|---|
| CN100408711C (en) * | 2002-06-25 | 2008-08-06 | 杰富意钢铁株式会社 | High-strength cold rolled steel sheet and process for producing the same |
| EP2610357A4 (en) * | 2010-08-23 | 2017-11-08 | Nippon Steel & Sumitomo Metal Corporation | Cold-rolled steel sheet and process for production thereof |
| CN102094149A (en) * | 2011-03-08 | 2011-06-15 | 攀钢集团钢铁钒钛股份有限公司 | Niobium-containing high-strength hot-galvanized steel plate and production method thereof |
| US10494693B2 (en) | 2015-03-25 | 2019-12-03 | Jfe Steel Corporation | High-strength steel sheet and method for producing the same |
| US10655194B2 (en) | 2015-03-25 | 2020-05-19 | Jfe Steel Corporation | High-strength steel sheet and method for producing the same |
| CN107429355B (en) * | 2015-03-25 | 2020-01-21 | 杰富意钢铁株式会社 | High-strength steel sheet and method for producing same |
| CN107406947A (en) * | 2015-03-25 | 2017-11-28 | 杰富意钢铁株式会社 | High-strength steel sheet and its manufacture method |
| CN107429355A (en) * | 2015-03-25 | 2017-12-01 | 杰富意钢铁株式会社 | High-strength steel sheet and its manufacture method |
| CN107923013B (en) * | 2015-08-19 | 2020-06-16 | 杰富意钢铁株式会社 | High-strength steel sheet and method for producing same |
| CN107923013A (en) * | 2015-08-19 | 2018-04-17 | 杰富意钢铁株式会社 | High-strength steel sheet and its manufacture method |
| CN106884119B (en) * | 2015-12-16 | 2019-03-26 | 上海梅山钢铁股份有限公司 | A kind of manufacturing method of thickness coating hot-dip galvanizing sheet steel |
| CN105925903A (en) * | 2016-04-27 | 2016-09-07 | 武汉钢铁股份有限公司 | Cold-rolled low-alloy high-strength steel for automobiles and production method thereof |
| CN106702267A (en) * | 2016-12-19 | 2017-05-24 | 武汉钢铁股份有限公司 | Iron-zinc coating steel plate with yield strength being 350 MPa grade and production method |
| CN106521341A (en) * | 2016-12-19 | 2017-03-22 | 武汉钢铁股份有限公司 | Iron-zinc coated steel plate with yield strength being 450 MPa and production method thereof |
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