CN100587096C - Alloyed hot-dip galvanized steel sheet and method for producing same - Google Patents
Alloyed hot-dip galvanized steel sheet and method for producing same Download PDFInfo
- Publication number
- CN100587096C CN100587096C CN200680010241A CN200680010241A CN100587096C CN 100587096 C CN100587096 C CN 100587096C CN 200680010241 A CN200680010241 A CN 200680010241A CN 200680010241 A CN200680010241 A CN 200680010241A CN 100587096 C CN100587096 C CN 100587096C
- Authority
- CN
- China
- Prior art keywords
- steel sheet
- following
- dip galvanized
- alloyed hot
- quality
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Expired - Fee Related
Links
Landscapes
- Heat Treatment Of Sheet Steel (AREA)
- Coating With Molten Metal (AREA)
Abstract
Disclosed is an alloyed hot-dip galvanized steel sheet having a chemical composition consisting of, in mass%, 0.05-0.25 % of C, not more than 2.0% of Si, 1-3% of Mn, not more than 0.1% of P, not morethan 0.01% of S, 0.3-2% of Al, less than 0.005% of N, not more than 1% of Cr, not more than 1% of V, not more than 1% of Mo, less than 0.005% of Ti, less than 0.005% of Nb and the balance of Fe and unavoidable impurities, while satisfying Si + Al = 0.6 % and Cr + V + Mo = 0.1-2%.
Description
Technical field
The present invention relates to high strength alloyed hot-dip zinc-coated steel plate of low yielding ratio type (hot dip galvannealed steel sheet) and the manufacture method thereof in purposes, used as automotive sheet.
Background technology
In recent years, from the environment viewpoint of preserving our planet, the raising of the specific fuel consumption of automobile becomes important topic.Therefore, realize thin-walled property by the high strength of car body materials, thereby the light-weighted activity of car body itself is become increasingly active.But, because the high strength of steel plate causes the reduction of ductility, the reduction of the processibility that promptly is shaped, thereby require to develop the material that has high strength and high working property concurrently.
Tackle this requirement, developed ferrite, martensite dual-phase steel (Dual-Phase steel) up to now, utilized the TRIP steel various complex tissue steel such as (transformation induced plasticity steel) of the phase change induction plasticity (transformationinduced plasticity) of residual austenite.
Described steel plate antirust when improving actual the use implemented plating sometimes as purpose on the surface, as plated steel sheet, from guaranteeing the viewpoint of stampability, spot weldability, application adaptation, the alloyed hot-dip galvanized steel sheet of the Fe of steel plate is spread in many uses in coating implementing thermal treatment after the pot galvanize, and this has been proposed various motions.
For example, in Japanese patent laid-open 11-279691 communique, thereby proposed to guarantee that by adding a large amount of Si remaining γ realizes the alloyed hot-dip galvanized steel sheet of the excellent processability of high ductibility.But, because Si makes the plating reduction, thereby when on this high Si steel, carrying out plating, need carry out the punching press plating of following complicated step: Ni, the coating of medicaments, or the oxide skin of reduction surface of steel plate, suitably controlled oxidation film thickness etc.
And, open in the 2002-030403 communique the Japanese Patent spy, proposed to improve the good alloyed hot-dip galvanized steel sheet of ductility of plating wettability and pulverability by replacing Si to add the Al less with respect to the plating detrimentally affect.But in the drawing of reality, except the raising of ductility, accurately the improvement of plasticity (shape fixability) also becomes big problem.
Make the steel plate high strength and yield strength is risen, the resilience quantitative change during drawing is big, and accurately plasticity reduces.The reduction of this accurate plasticity can recently improve by reducing surrender, opens the cold-rolled steel sheet that has proposed the low yielding ratio type in the 2002-317249 communique the Japanese Patent spy.But, when this steel plate is applied to alloyed hot-dip galvanized steel sheet,, thereby be difficult to reach low yielding ratio because the temperature that zinc is bathed must be to surpass 450 ℃ high temperature, and need surpass 500 ℃ Alloying Treatment.
And open the Japanese Patent spy and to have proposed following hot-dip galvanizing sheet steel in the 2004-115843 communique: by making Si, Al and Mn content balance, and the annealing back keeps the short period of time with low temperature and obtains containing the martensitic phase of a large amount of C, thereby has low yielding ratio.But this technology that is proposed is the technology of relevant DP steel, and the DP steel be owing to can not make full use of the raising (TRIP effect) of the ductility that the strain-induced phase transformation of residual austenite causes, thereby is difficult to think to have sufficient ductility.
Summary of the invention
The object of the present invention is to provide a kind of high-strength hot-dip zinc-coated steel sheet and manufacture method thereof, it just can access good alloyed zinc hot dip galvanized property without complicated step, can realize good ductility and low yielding ratio in alloyed zinc hot dip galvanized back.Wherein, in the present invention, " high strength " is meant to have the intensity of TS more than 340MPa.
The inventor etc. have carried out research with keen determination in order to obtain the good high strength alloyed hot-dip zinc-coated steel plate of low yielding ratio type of ductility from the composition of steel plate and the viewpoint of microtexture.Its result, discovery can reduce the yield ratio in the alloyed hot-dip galvanized steel sheet significantly by and interpolation Cr, V compound with Al, Mo, can reach yield ratio below 55%, and by suitably adjusting the amount of C, Si, Mn, Al, do not make the reduction of alloyed zinc hot dip galvanized property just can increase residual austenite, obtain good ductility.
Though become the reason of low yielding ratio about the compound interpolation by Al and Cr, V, Mo not clear and definite as yet, thinks following reason.That is, Al makes the solid solution C in the ferrite discharge mutually to the 2nd, thereby acts on ferritic purification effectively, and yield ratio is reduced.On the other hand, can handle with the austempering between high temperature, short time by adding Cr, V, Mo and produce residual austenite.Solid solution C in the residual austenite of Chan Shenging amount is less like this, becomes martensite mutually with less dependent variable, forms strain field on every side and yielding stress is reduced at it.The reduction of the yielding stress that the formation of this strain field causes owing to cause around making ferritic that solid solution C reduces add purifying by Al, thereby is thought and is more effectively produced.
The present invention finishes according to above-mentioned opinion, and following (1)～(18) are provided.
(1) a kind of alloyed hot-dip galvanized steel sheet, wherein, in quality %, comprise that C:0.05～0.25%, Si:2.0% are following, Mn:1～3%, P:0.1% is following, S:0.01% is following, Al:0.3～2%, N: less than 0.005%, Cr:1% is following, V:1% is following, Mo:1% is following, Ti: less than 0.005%, Nb: less than 0.005%, and satisfy Si+Al 〉=0.6%, Cr+V+Mo:1～2%, surplus is made of Fe and unavoidable impurities.
(2) a kind of alloyed hot-dip galvanized steel sheet, wherein, in quality %, comprise that C:0.05～0.25%, Si:2.0% are following, Mn:1～3%, P:0.1% is following, S:0.01% is following, Al:0.3～2%, N: less than 0.005%, Cr:1% is following, V:1% is following, Mo:1% is following, Ti: less than 0.005%, Nb: less than 0.005%, and satisfy Si+Al 〉=0.6%, (0.003 * Al) %, Cr+V+Mo:0.1～2%, surplus is made of Fe and unavoidable impurities N≤0.007%-.
(3) above-mentioned (1) described alloyed hot-dip galvanized steel sheet wherein, in quality %, and then contains a kind or 2 kinds that B:0.005% is following, Ni:1% is following.
(4) above-mentioned (2) described alloyed hot-dip galvanized steel sheet wherein, in quality %, and then contains a kind or 2 kinds that B:0.005% is following, Ni:1% is following.
(5) above-mentioned (1) described alloyed hot-dip galvanized steel sheet wherein, in quality %, and then contains the Ca that amounts to below 0.01% and a kind or 2 kinds of REM.
(6) above-mentioned (2) described alloyed hot-dip galvanized steel sheet wherein, in quality %, and then contains the Ca that amounts to below 0.01% and a kind or 2 kinds of REM.
(7) above-mentioned (3) described alloyed hot-dip galvanized steel sheet wherein, in quality %, and then contains the Ca that amounts to below 0.01% and a kind or 2 kinds of REM.
(8) above-mentioned (4) described alloyed hot-dip galvanized steel sheet wherein, in quality %, and then contains the Ca that amounts to below 0.01% and a kind or 2 kinds of REM.
(9) each described alloyed hot-dip galvanized steel sheet in above-mentioned (1) to (8), wherein, the metal structure of above-mentioned steel plate contains counts 3～20% residual austenite phase with volume fraction.
(10) a kind of manufacture method of alloyed hot-dip galvanized steel sheet, it comprises following operation: cold-rolled steel sheet is annealed 730～900 ℃ temperature province, described cold-rolled steel sheet is in quality %, comprise C:0.05～0.25%, below the Si:2%, Mn:1～3%, below the P:0.1%, below the S:0.01%, Al:0.3～2%, N: less than 0.005%, below the Cr:1%, below the V:1%, below the Mo:1%, Ti: less than 0.005%, Nb: less than 0.005%, surplus is made of Fe and unavoidable impurities, and satisfies Si+Al 〉=0.6%, Cr+V+Mo:0.1～2%; Cold-rolled steel sheet after the annealing is cooled off with 3～100 ℃/second speed of cooling; The temperature province of cooled cold-rolled steel sheet at 350～600 ℃ kept 30～250 seconds; Cold-rolled steel sheet after keeping is carried out pot galvanize; And with the temperature alloying of the cold-rolled steel sheet after the pot galvanize with 470～600 ℃.
(11) a kind of manufacture method of alloyed hot-dip galvanized steel sheet, it comprises following operation: cold-rolled steel sheet is annealed 730～900 ℃ temperature province, described cold-rolled steel sheet is in quality %, comprise C:0.05～0.25%, below the Si:2%, Mn:1～3%, below the P:0.1%, below the S:0.01%, Al:0.3～2%, N: less than 0.005%, below the Cr:1%, below the V:1%, below the Mo:1%, Ti: less than 0.005%, Nb: less than 0.005%, surplus is made of Fe and unavoidable impurities, and satisfies Si+Al 〉=0.6%, N≤0.007%-(0.003 * Al) %, Cr+V+Mo:0.1～2%; Cold-rolled steel sheet after the annealing is cooled off with 3～100 ℃/second speed of cooling; The temperature province of cooled cold-rolled steel sheet at 350～600 ℃ kept 30～250 seconds; Cold-rolled steel sheet after keeping is carried out pot galvanize; And with the temperature alloying of the cold-rolled steel sheet after the pot galvanize with 470～600 ℃.
(12) manufacture method of above-mentioned (10) described alloyed hot-dip galvanized steel sheet, wherein, above-mentioned cold-rolled steel sheet is in quality %, and then contains a kind or 2 kinds that B:0.005% is following, Ni:1% is following.
(13) manufacture method of above-mentioned (11) described alloyed hot-dip galvanized steel sheet, wherein, above-mentioned cold-rolled steel sheet is in quality %, and then contains a kind or 2 kinds that B:0.005% is following, Ni:1% is following.
(14) manufacture method of above-mentioned (10) described alloyed hot-dip galvanized steel sheet, wherein, above-mentioned cold-rolled steel sheet is in quality %, and then contains the Ca that amounts to below 0.01% and a kind or 2 kinds of REM.
(15) manufacture method of above-mentioned (11) described alloyed hot-dip galvanized steel sheet, wherein, above-mentioned cold-rolled steel sheet is in quality %, and then contains the Ca that amounts to below 0.01% and a kind or 2 kinds of REM.
(16) manufacture method of above-mentioned (12) described alloyed hot-dip galvanized steel sheet, wherein, above-mentioned cold-rolled steel sheet is in quality %, and then contains the Ca that amounts to below 0.01% and a kind or 2 kinds of REM.
(17) manufacture method of above-mentioned (13) described alloyed hot-dip galvanized steel sheet, wherein, above-mentioned cold-rolled steel sheet is in quality %, and then contains the Ca that amounts to below 0.01% and a kind or 2 kinds of REM.
(18) manufacture method of each the described alloyed hot-dip galvanized steel sheet in above-mentioned (10) to (17), wherein, above-mentioned alloyed hot-dip galvanized steel sheet contains counts 3～20% residual austenite phase with volume fraction.
According to the present invention, just can access good alloyed zinc hot dip galvanized property without complicated step, can reach the low yielding ratio below good ductility and 55% after alloyed zinc hot dip galvanized.
Embodiment
Below, the present invention is specifically described.
At first, the composition qualification reason to alloyed hot-dip galvanized steel sheet of the present invention describes.% refers to quality % in the following description.
C：0.05～0.25％
C is the element that makes austenite stable, is to guarantee the necessary element of residual austenite.During C quantity not sufficient 0.05%, be difficult to when guaranteeing armor plate strength, guarantee remained austenite content and reach high ductibility.On the other hand, the C amount surpasses at 0.25% o'clock, and the sclerosis of weld part and heat affected zone is remarkable, the weldability variation.Thus, C amount is made as 0.05～0.25% scope.
Below the Si:2.0%
Si is the reinforcement effective elements to steel.And be the ferrite generting element, owing to promote the multiviscosisty of C in austenite and the generation that suppresses carbide, thereby have the effect of the generation that promotes residual austenite.The Si amount is preferably more than 0.01%.The Si amount surpasses at 2.0% o'clock, causes the deterioration of plating.Therefore, the Si amount is made as below 2.0%.Be preferably below 0.5%.
Mn：1～3％
Mn is the reinforcement effective elements to steel.And being the element that makes austenite stable, is to increase the necessary element of residual austenite.But, during Mn quantity not sufficient 1%, be difficult to obtain this effect, on the other hand, surpass at 3% o'clock, because of the increase of over-drastic the 2nd phase per-cent and the increase of solution strengthening amount cause intensity to rise significantly, cause the reduction of ductility.Therefore, Mn amount is made as 1～3% scope.
Below the P:0.1%
Though P is the reinforcement effective elements to steel, surpass at 0.1% o'clock, because of grain boundary segregation causes embrittlement, make the impact characteristics variation.Therefore, the P amount is made as below 0.1%.
Below the S:0.01%
S forms inclusion such as MnS and becomes the deterioration of shock-resistant characteristic or along the reason of the crackle of the metal flow of weld part, thereby preferably reduces as far as possible, but considers to be made as below 0.01% from the aspect of manufacturing cost.
Al：0.3～2％
Al acts on ferritic purification effectively, and the yield ratio of steel is reduced.But during Al quantity not sufficient 0.3%, this effect is insufficient.On the other hand, the Al amount surpasses at 2% o'clock, and it is many that the inclusion in the steel plate becomes, thereby make the ductility variation.Therefore, Al amount is made as 0.3～2% scope.
Si+Al≥0.6％
Al and Si are the ferrite generting element equally, owing to promote the multiviscosisty of C in ferrite, and suppress the generation of carbide, and thereby have the effect of the generation that promotes residual austenite.And this effect is insufficient when the total less than 0.6% of Al and Si amount, thereby can not obtain sufficient ductility.Therefore, Si+Al is made as more than 0.6%.And Si+Al is preferably below 3%.
N: less than 0.005%
N is a unavoidable impurities, forms nitride.Its amount is 0.005% when above, can cause ductility reduction under high temperature and low temperature because of forming nitride.Therefore, N amount is made as is lower than 0.005%.
N≤0.007％-(0.003×Al)％
When increasing the amount of the separating out increase that makes AlN along with the N amount, the crackle of steel billet when causing continuous casting easily.Therefore, under the situation of the crackle of steel billet when needs prevent continuous casting,, on the basis that makes N quantity not sufficient 0.005%, also to satisfy N≤0.007%-(0.003 * Al) % in order to prevent crackle of steel billet.
Cr, V, Mo: respectively below 1%
Cr+V+Mo：0.1～2％
Cr, V, Mo are the low yielding ratio effective elements to steel.This effect becomes remarkable by compound interpolation Al.But its effect is saturated when adding above 1% respectively.And this effect is insufficient when the total less than 0.1% of Cr, V, Mo, and it totals at 2% o'clock on the contrary, may cause the reduction of ductility and the deterioration of plating because of over-drastic intensity rises.Therefore, make Cr, V, Mo, its total is made as 0.1～2% respectively below 1%.Be preferably 0.15～1.3%.
Ti, Nb: difference less than 0.005%
Ti, Nb form carbonitride and separate out, thereby steel is strengthened.But this precipitation strength increases yielding stress, and is unfavorable to low yielding ratioization.And, being increased in separately addition 0.005% and just can manifesting when above of this yielding stress.Therefore, establish Ti, Nb amount less than 0.005% respectively.
Below the B:0.005%
Because B acts on the reinforcement of steel effectively, thereby can add as required.But, surpasses 0.005% o'clock intensity and excessively rise, thereby processibility reduces.Therefore, under the situation of adding B, make its amount below 0.005%.
Below the Ni:1%
Ni is an austenite stabilizer element, owing to make austenite residual and effective to the intensity rising, thereby can add as required.But its effect is saturated when adding above 1%, causes the rising of cost on the contrary.Therefore, under the situation of adding Ni, establish its amount below 1%.
Ca or REM:1 kind or 2 kinds of totals are below 0.01%
Ca and REM have the effect of the form of the sulfide-based inclusion of control, therefore, have the effect of the stretch flange raising that makes steel plate, thereby can add as required.This effect described Ca and REM total over 0.01% o'clock saturated.Therefore, adding under the situation of Ca, REM, the total of establishing its a kind or 2 kinds is below 0.01%.
In addition, except the Fe of above element and surplus, in manufacturing processed, sneak into the trace element of necessary interpolation in various impurity elements and the manufacturing processed etc. inevitably, but this unavoidable impurities can be not influential especially to effect of the present invention, thereby allow.
Then, the metal structure to steel plate describes.
Residual austenite phase: count 3～20% with volume fraction
In the present invention, residual austenite acts on the strain-induced phase transformation mutually effectively, is necessary in order to obtain high ductibility, and the control of its volume fraction is extremely important.In the present invention, from guaranteeing the viewpoint of high ductibility, residual austenite is mutually preferably at least more than 3%.On the other hand, surpass under 20% the situation mutually residual austenite, because the back that is shaped produces a large amount of martensite, it is big that fragility becomes, and fragility need be suppressed in the allowed band, thereby remained austenite content is preferably below 20%.As the metal structure of steel plate of the present invention, by as the ferritic phase of principal phase with comprise residual austenite the 2nd phase composite mutually, from guaranteeing the viewpoint of high ductibility, the volume fraction of ferritic phase is preferably 40～90%.And as the 2nd phase beyond the residual austenite phase, the total of the volume fraction of bainite phase, martensitic phase, perlite phase is preferably 7～50%.
Then, creating conditions of alloyed hot-dip galvanized steel sheet of the present invention described.
In the present invention, the steel that the melting mentioned component is formed is made steel billet by continuous casting, carries out hot rolling, cold rolling, but described condition does not limit especially.Then, anneal with 730～900 ℃ temperature province,, after 350～600 ℃ temperature provinces kept 30～250 seconds, and carried out pot galvanize then, carry out alloying with 470～600 ℃ with 3～100 ℃/s cooling at the continuously dip coat production line.
Annealing temperature: 730～900 ℃
2 regions at austenite one phase or austenite phase and ferritic phase are annealed, but under the situation of 730 ℃ of annealing temperature less thaies, exist the situation of the insufficient fusion of carbide in the steel plate, ferritic recrystallize not to finish and can not obtain the situation of target property.On the other hand, surpass under 900 ℃ the situation, exist the austenite particulate to grow up significantly, cause by what produce to begin the situation that ferritic nucleation site reduces mutually from the 2nd by cooling afterwards in annealing temperature.Therefore, annealing temperature is 730～900 ℃.
Speed of cooling: 3～100 ℃/s
Under the situation of 3 ℃/s of speed of cooling less than, owing to separate out perlite in a large number, the amount of the solid solution C in the transformed austenite does not reduce significantly, thereby has the situation that can not obtain destination organization.And speed of cooling surpasses under the situation of 100 ℃/s, because ferritic growth is suppressed, ferritic volume fraction significantly reduces, thereby has the situation that can not guarantee sufficient ductility.Therefore, speed of cooling is 3～100 ℃/s.
Keep temperature: 350～600 ℃
Keeping temperature to surpass under 600 ℃ the situation, never carbide precipitate in the transformed austenite, on the contrary, under the situation of 350 ℃ of less thaies, because of bottom bainitic transformation carbide precipitate in bainite ferrite, thereby all can not obtain stable residual austenite fully.Therefore, keeping temperature is 350～600 ℃.In order stably to produce residual austenite, preferably below 500 ℃.
Hold-time: 30～250 seconds
Hold-time is relevant with the control of residual austenite, plays a very important role.That is, under 30 seconds situation of hold-time less than,, can not guarantee remained austenite content, thereby can not obtain desirable characteristic owing to can not advance the not stabilization of transformed austenite.On the other hand, surpass under 250 seconds the situation in the hold-time, can not obtain the few austenite phase of solid solution C amount, be difficult to become martensitic phase mutually, be difficult to obtain low yielding stress by the strain field that around it, produces with less dependent variable as purpose of the present invention.Therefore, the hold-time is 30～250 seconds.Never the viewpoint of transformed austenite stabilization is set out, and the hold-time preferably surpasses 60 seconds, and then preferably above 90 seconds.And, reduce in order to make yielding stress, be preferably below 200 seconds.
Alloying Treatment temperature: 470～600 ℃
After above-mentioned maintenance is handled, and then therefore the Alloying Treatment temperature of implementing after the pot galvanize need be set and be limited to 470 ℃ more than the plating bath temperature.And when the alloying temperature surpassed 600 ℃, the situation that surpasses 600 ℃ with above-mentioned maintenance temperature was identical, carbide precipitate in the transformed austenite never, thus can not obtain stable residual austenite.Therefore, the Alloying Treatment temperature is 470～600 ℃.
In addition, the annealing temperature of regulation, maintenance temperature, Alloying Treatment temperature keep temperature to need not to remain unchanged as long as in above-mentioned scope in of the present invention creating conditions.And, under the situation that speed of cooling changes in cooling, as long as in above-mentioned scope.And, about the plating condition, as long as in common operating restraint, as long as coating amount is at 20～70g/m
2, the amount of the Fe in the coating is about 6～15% to get final product.
Embodiment
Below, embodiments of the invention are described.
Melt out the steel of forming shown in the table 1 with converter, make steel billet by continuous casting.The crackle of the steel billet of expression this moment having or not of producing in the lump in table 1.To the generation of crackle, the judgement of after steel billet being cooled to room temperature, carrying out, also carry out the judgement under the dye check with range estimation.
After resulting steel billet is heated to 1250 ℃, carry out hot rolling for 900 ℃, make the hot-rolled steel sheet that thickness of slab is 3.0mm with finishing temperature.After the hot rolling, carry out pickling, and then carry out cold rolling and make the cold-rolled steel sheet that thickness of slab is 1.2mm.Then, after Continuous Hot Dip Galvanizing Line is heat-treated with the condition shown in the table 2, implement 50/50g/m
2Plating implement Alloying Treatment so that the Fe in coating amount becomes 9% mode.
About resulting steel plate, implement 0.5% temper rolling, and the investigation mechanical characteristics.As mechanical characteristics, use the JIS5 tension test sheet of choosing from steel plate along rolling right angle orientation, measure yielding stress YS, tensile strength TS, stretchiness EL.Tension test is with Deformation velocity 6.7 * 10
-3s
-1Carry out.The value of in table 2, representing described measured value and yield ratio YR and TS * EL in the lump.
Steel plate No.1 of the present invention, 2,5～8,11～16,18,21,22,24,28 as shown in table 2, as to satisfy composition of the present invention and create conditions, yield ratio is all represented the value below 55%, tensile strength TS, stretchiness EL also represent value fully.With respect to this, the comparison steel plate No.3,4,9,10,17,19,20,23,25～27,29～38 that breaks away from composition of the present invention and create conditions, yield ratio YR, tensile strength TS, stretchiness EL and described equilibrated break away from preferable range more than one.And as shown in table 1, (A～L of 0.003 * Al) %, crackle of steel billet do not have to produce to satisfy N≤0.007%-in the steel plate of the present invention.
Claims (16)
1. alloyed hot-dip galvanized steel sheet, wherein, in quality %, comprise C:0.05～0.25%, below the Si:2.0%, Mn:1～3%, below the P:0.1%, below the S:0.01%, Al:0.3～2%, N: less than 0.005%, below the Cr:1%, below the V:1%, below the Mo:1%, Ti: less than 0.005%, Nb: less than 0.005%, and satisfy Si+Al 〉=0.6%, Cr+V+Mo:0.1～2%, surplus is made of Fe and unavoidable impurities, and contain and count 3～20% residual austenite phase with volume fraction, yield ratio is below 55%.
2. alloyed hot-dip galvanized steel sheet, wherein, in quality %, comprise C:0.05～0.25%, below the Si:2.0%, Mn:1～3%, below the P:0.1%, below the S:0.01%, Al:0.3～2%, N: less than 0.005%, below the Cr:1%, below the V:1%, below the Mo:1%, Ti: less than 0.005%, Nb: less than 0.005%, and satisfy Si+Al 〉=0.6%, N≤0.007%-(0.003 * Al) %, Cr+V+Mo:0.1～2%, surplus is made of Fe and unavoidable impurities, and contain and count 3～20% residual austenite phase with volume fraction, yield ratio is below 55%.
3. alloyed hot-dip galvanized steel sheet according to claim 1 wherein, in quality %, and then contains a kind or 2 kinds that B:0.005% is following, Ni:1% is following.
4. alloyed hot-dip galvanized steel sheet according to claim 2 wherein, in quality %, and then contains a kind or 2 kinds that B:0.005% is following, Ni:1% is following.
5. alloyed hot-dip galvanized steel sheet according to claim 1 wherein, in quality %, and then contains the Ca that amounts to below 0.01% and a kind or 2 kinds of REM.
6. alloyed hot-dip galvanized steel sheet according to claim 2 wherein, in quality %, and then contains the Ca that amounts to below 0.01% and a kind or 2 kinds of REM.
7. alloyed hot-dip galvanized steel sheet according to claim 3 wherein, in quality %, and then contains the Ca that amounts to below 0.01% and a kind or 2 kinds of REM.
8. alloyed hot-dip galvanized steel sheet according to claim 4 wherein, in quality %, and then contains the Ca that amounts to below 0.01% and a kind or 2 kinds of REM.
9. one kind contains with volume fraction and counts 3～20% residual austenite phase, the yield ratio manufacture method at the alloyed hot-dip galvanized steel sheet below 55%, and it comprises following operation:
Cold-rolled steel sheet is annealed 730～900 ℃ temperature province, described cold-rolled steel sheet is in quality %, comprise that C:0.05～0.25%, Si:2% are following, Mn:1～3%, P:0.1% is following, S:0.01% is following, Al:0.3～2%, N: less than 0.005%, Cr:1% is following, V:1% is following, Mo:1% is following, Ti: less than 0.005%, Nb: less than 0.005%, surplus is made of Fe and unavoidable impurities, and satisfies Si+Al 〉=0.6%, Cr+V+Mo:0.1～2%;
Cold-rolled steel sheet after the annealing is cooled off with 3～100 ℃/second speed of cooling;
The temperature province of cooled cold-rolled steel sheet at 350～600 ℃ kept 30～250 seconds;
Cold-rolled steel sheet after keeping is carried out pot galvanize; And
With the temperature alloying of the cold-rolled steel sheet after the pot galvanize with 470～600 ℃.
10. one kind contains with volume fraction and counts 3～20% residual austenite phase, the yield ratio manufacture method at the alloyed hot-dip galvanized steel sheet below 55%, and it comprises following operation:
Cold-rolled steel sheet is annealed 730～900 ℃ temperature province, described cold-rolled steel sheet is in quality %, comprise that C:0.05～0.25%, Si:2% are following, Mn:1～3%, P:0.1% is following, S:0.01% is following, Al:0.3～2%, N: less than 0.005%, Cr:1% is following, V:1% is following, Mo:1% is following, Ti: less than 0.005%, Nb: less than 0.005%, surplus is made of Fe and unavoidable impurities, and satisfies Si+Al 〉=0.6%, N≤0.007%-(0.003 * Al) %, Cr+V+Mo:0.1～2%;
Cold-rolled steel sheet after the annealing is cooled off with 3～100 ℃/second speed of cooling;
The temperature province of cooled cold-rolled steel sheet at 350～600 ℃ kept 30～250 seconds;
Cold-rolled steel sheet after keeping is carried out pot galvanize; And
With the temperature alloying of the cold-rolled steel sheet after the pot galvanize with 470～600 ℃.
11. the manufacture method of alloyed hot-dip galvanized steel sheet according to claim 9, wherein, described cold-rolled steel sheet is in quality %, and then contains a kind or 2 kinds that B:0.005% is following, Ni:1% is following.
12. the manufacture method of alloyed hot-dip galvanized steel sheet according to claim 10, wherein, described cold-rolled steel sheet is in quality %, and then contains a kind or 2 kinds that B:0.005% is following, Ni:1% is following.
13. the manufacture method of alloyed hot-dip galvanized steel sheet according to claim 9, wherein, described cold-rolled steel sheet is in quality %, and then contains the Ca that amounts to below 0.01% and a kind or 2 kinds of REM.
14. the manufacture method of alloyed hot-dip galvanized steel sheet according to claim 10, wherein, described cold-rolled steel sheet is in quality %, and then contains the Ca that amounts to below 0.01% and a kind or 2 kinds of REM.
15. the manufacture method of alloyed hot-dip galvanized steel sheet according to claim 11, wherein, described cold-rolled steel sheet is in quality %, and then contains the Ca that amounts to below 0.01% and a kind or 2 kinds of REM.
16. the manufacture method of alloyed hot-dip galvanized steel sheet according to claim 12, wherein, described cold-rolled steel sheet is in quality %, and then contains the Ca that amounts to below 0.01% and a kind or 2 kinds of REM.
Applications Claiming Priority (3)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2005103832 | 2005-03-31 | ||
| JP103832/2005 | 2005-03-31 | ||
| JP058458/2006 | 2006-03-03 |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN101151390A CN101151390A (en) | 2008-03-26 |
| CN100587096C true CN100587096C (en) | 2010-02-03 |
Family
ID=39251265
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN200680010241A Expired - Fee Related CN100587096C (en) | 2005-03-31 | 2006-03-31 | Alloyed hot-dip galvanized steel sheet and method for producing same |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN100587096C (en) |
Families Citing this family (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP2402472B2 (en) * | 2010-07-02 | 2017-11-15 | ThyssenKrupp Steel Europe AG | High-tensile, cold formable steel and flat steel product composed of such steel |
| BR112015007044B1 (en) * | 2012-10-03 | 2020-11-10 | Nippon Steel Corporation | galvanized steel sheet with annealing and method to produce the same |
| CN111971410A (en) * | 2018-03-30 | 2020-11-20 | Ak钢铁产权公司 | Low-alloy third-generation advanced high-strength steel and manufacturing method |
| CN109023054A (en) * | 2018-08-16 | 2018-12-18 | 攀钢集团攀枝花钢铁研究院有限公司 | Hot-dip galvanizing sheet steel and its manufacturing method |
| CN111434443B (en) * | 2019-07-03 | 2022-02-22 | 苏州普热斯勒先进成型技术有限公司 | Method and device for manufacturing automobile structural part |
-
2006
- 2006-03-31 CN CN200680010241A patent/CN100587096C/en not_active Expired - Fee Related
Also Published As
| Publication number | Publication date |
|---|---|
| CN101151390A (en) | 2008-03-26 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN101932742B (en) | High-strength hot-dip-galvanized steel sheet having excellent moldability, and method for production thereof | |
| CN101155939B (en) | High-strength cold-rolled steel sheet excellent in uniform elongation and method for manufacturing same | |
| CN101821419B (en) | High-strength hot-dip zinc plated steel sheet excellent in workability and process for manufacturing the same | |
| CN101939457B (en) | High strength galvanized steel sheet with excellent formability and method for manufacturing the same | |
| CN102803540B (en) | High-strength Hot-dip Galvannealed Steel Shhet With Excellent Workability And Fatigue Characteristics And Process For Production Thereof | |
| CN102959116B (en) | High-strength hot-dip galvanized steel sheet with excellent processability and process for producing same | |
| CN103890202B (en) | The manufacture method of the high tensile steel plate of excellent processability | |
| CN101932746B (en) | High-strength steel sheet and process for production thereof | |
| CN102149840B (en) | High-strength steel plate and manufacturing method thereof | |
| CN103146992B (en) | The high-strength hot-dip zinc-coated steel sheet of excellent processability | |
| KR101422556B1 (en) | Method for producing high-strength steel sheet | |
| CN102859018B (en) | High-strength hot-dip galvanized steel sheet with excellent formability and impact resistance, and process for producing same | |
| KR101328768B1 (en) | Method for manufacturing very high strength, cold-rolled, dual phase steel sheets, and sheets thus produced | |
| CN103339280B (en) | Excellent processability also has high strength cold rolled steel plate and the manufacture method thereof of high yield ratio | |
| CN104364408B (en) | Alloyed hot-dip zinc-coated hot rolled steel plate and manufacture method thereof | |
| CA2601497C (en) | Galvannealed steel sheet and method for producing the same | |
| CN103998639B (en) | Yield-ratio high-strength cold-rolled steel sheet and its manufacture method | |
| CN102348821A (en) | High-strength hot-dip galvanized steel sheet having excellent formability and method for producing same | |
| CN101939456A (en) | High strength galvanized steel sheet with excellent formability and method for manufacturing the same | |
| CN103361577B (en) | The high yield ratio and high-strength steel plate of excellent in workability | |
| CN103842540A (en) | Hot-dip galvanized steel sheet and method for producing same | |
| CN106574337A (en) | High-strength hot-dip zinc-coated steel sheet and method for producing same | |
| CN101802233A (en) | Dual phase steel, by the flat product of this dual phase steel preparation and the method for preparing flat product | |
| CN102149841A (en) | High-strength steel sheet and method for production thereof | |
| CN102712978B (en) | High-strength hot-dip galvanized steel sheet with excellent processability and spot weldability and process for producing same |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| C06 | Publication | ||
| PB01 | Publication | ||
| C10 | Entry into substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| C14 | Grant of patent or utility model | ||
| GR01 | Patent grant | ||
| CF01 | Termination of patent right due to non-payment of annual fee | ||
| CF01 | Termination of patent right due to non-payment of annual fee |
Granted publication date: 20100203 |