CN100526493C - High young's modulus steel plate, zinc hot dip galvanized steel sheet using the same, alloyed zinc hot dip galvanized steel sheet, high young's modulus steel pipe, and method for production thereof - Google Patents
High young's modulus steel plate, zinc hot dip galvanized steel sheet using the same, alloyed zinc hot dip galvanized steel sheet, high young's modulus steel pipe, and method for production thereof Download PDFInfo
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- CN100526493C CN100526493C CNB2005800251600A CN200580025160A CN100526493C CN 100526493 C CN100526493 C CN 100526493C CN B2005800251600 A CNB2005800251600 A CN B2005800251600A CN 200580025160 A CN200580025160 A CN 200580025160A CN 100526493 C CN100526493 C CN 100526493C
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Abstract
An embodiment of a high Young's modulus steel sheet, wherein it has a chemical composition, in mass %, that C: 0.0005 to 0.30 %, Si: 2.5 % or less, Mn: 2.7 to 5.0 %, P: 0.15 % or less, S: 0.015 % or less, Mo: 0.15 to 1.5 %, B: 0.0006 to 0.01%, Al: 0.15 % or less, and the balance: Fe and inevitable impurities.
Description
Technical field
The present invention relates to high young's modulus steel plate, used its hot-dip galvanized steel sheet, alloyed hot-dip galvanized steel plate and high Young's modulus steel pipe and their manufacture method.
The application is to the Japanese patent application 2005-207043 of the Japanese patent application 2004-218132 of application on July 27th, 2004, the Japanese patent application 2004-330578 of application on November 15th, 2004, the Japanese patent application 2005-019942 of application on January 27th, 2005, application on July 15th, 2005, advocate right of priority, quote their content at this.
Background technology
About improving the technology of Young's modulus, a lot of reports were arranged once so far.Wherein major part relate to improve rolling direction (RD) and with the technology of the Young's modulus of the vertical width of rolling direction (RD) (TD).
All disclose in patent documentation 1～9 grade and passed through at α+γ
2Phase region is rolled and improves the technology of the Young's modulus of TD direction.
Disclose in the patent documentation 10 by the top layer is applied and be lower than Ar
3Phase point temperature rolling and improve the technology of the Young's modulus of TD direction.
On the other hand, also disclose and related in the Young's modulus that improves the TD direction, also improved the technology of the Young's modulus of RD direction.That is, disclosedly in the patent documentation 11 be, except being rolled, by implementing the rolling Young's modulus that improves the two with the perpendicular width of this direction at certain orientation.But, in the continuously hot rolling technology of thin plate, change rolling direction midway and hinder productivity significantly, therefore also unrealistic.
Relate to the high cold-rolled steel sheet of Young's modulus though patent documentation 12 discloses, this also is not to be the Young's modulus height of RD direction at the Young's modulus height of TD direction.
In addition, patent documentation 13 discloses the technology that compound interpolation Mo, Nb, B improve Young's modulus, but because hot-rolled condition is different fully, so the Young's modulus height of TD direction and be not the Young's modulus height of RD direction.
As mentioned above, exist in the past and be called the steel plate of high Young's modulus, but all be the high steel plate of Young's modulus with the vertical width of rolling direction (RD) (TD).Yet the width of steel plate is to the maximum about 2m, and with the direction of the Young's modulus maximum occasion as the length direction of member, its length can not reach more than the width.Therefore, for long member, urgently wish the high steel plate of Young's modulus of rolling direction.And, with regard to manufacture method, also be that the hot rolling with the α+γ district of fluctuating easily at rolling reactive force is a prerequisite, existing problems aspect productivity.
Steel plate is processed into automobile with and the occasion of the parts used of building materials, shape freezing becomes the problem of maximum.For example, carry out after the bending machining when removing load, the rebound phenomenon that steel plate recovers original form takes place, and therefore has the problem that can not obtain desired shape.This phenomenon is accompanied by high strength and becomes obviously, the obstacle when becoming high tensile steel plate and being applicable to member.
Patent documentation 1: the spy opens clear 59-83721 communique
Patent documentation 2: the spy opens flat 5-263191 communique
Patent documentation 3: the spy opens flat 8-283842 communique
Patent documentation 4: the spy opens flat 8-311541 communique
Patent documentation 5: the spy opens flat 9-53118 communique
Patent documentation 6: the spy opens flat 4-136120 communique
Patent documentation 7: the spy opens flat 4-141519 communique
Patent documentation 8: the spy opens flat 4-147916 communique
Patent documentation 9: the spy opens flat 4-293719 communique
Patent documentation 10: the spy opens flat 4-143216 communique
Patent documentation 11: the spy opens flat 4-147917 communique
Patent documentation 12: the spy opens flat 5-255804 communique
Patent documentation 13: the spy opens flat 08-1311541 communique
Summary of the invention
The present invention In view of the foregoing proposes, and its purpose is: steel plate, the hot-dip galvanized steel sheet that has used it, alloyed hot-dip galvanized steel plate and high Young's modulus steel pipe and their manufacture method that the good high Young's modulus of the Young's modulus of rolling direction (RD) is provided.
The present inventor concentrates on studies in order to realize above-mentioned target, obtains the opinion that the past of the following stated does not have.
Promptly, by making C, Si, Mn, P, S, Mo, B and the Al that contains specified amount, perhaps contain the texture prosperity of near surface regulation of the steel of C, Si, Mn, P, S, Mo, B, Al, N, Nb and Ti, thereby the invention of the high steel plate of the Young's modulus of rolling direction has been obtained success.
And the steel plate that is obtained by the present invention obtains extra high Young's modulus more than the 240GPa near surface, so flexural rigidity significantly improves, and for example shape freezing significantly improves.Following the property the freezed undesirable level of its resilience of high strength etc. to become big essential factor is: the amount of returning after the load that applies during the pressing machine distortion is removed is very big.Therefore,, the amount of returning can be suppressed, resilience may be lowered if improve Young's modulus.In addition, when flexural deformation, therefore near the deformational behavior the very big top layer of moment of flexure improves by the Young's modulus that only makes the top layer shape freezing generation remarkable influence, may improve significantly.
The present invention is based on such thought and brand-new opinion is constructed, unprecedented brand-new steel plate and manufacture method thereof, and its main idea is as follows.
(1). a kind of high young's modulus steel plate, it is characterized in that, in quality % contain C:0.0005～0.30%, below the Si:2.5%, Mn:2.7～5.0%, below the P:0.15%, below the S:0.015%, Mo:0.15～1.5%, B:0.0006～0.01%, below the Al:0.15%, and surplus is made of Fe and unavoidable impurities, 1/8 layer of thickness of slab 110}＜223〉with 110}＜111〉the utmost point density of either party or the two be more than 10, the Young's modulus of rolling direction surpasses 230GPa.
(2). according to (1) described high young's modulus steel plate, it is characterized in that, 1/2 layer of thickness of slab 112}＜110〉and utmost point density be more than 6.
(3). according to (1) described high young's modulus steel plate, it is characterized in that, also contain a kind or 2 kinds among Ti:0.001～0.20 quality %, Nb:0.001～0.20 quality %.
(4). according to (1) described high young's modulus steel plate, it is characterized in that, deduct the BH amount (MPa) that the difference of the flow stress that stretched estimates at 2% o'clock by the upper yield point of 2% back when implementing thermal treatments in 20 minutes and carrying out tension test once again for 170 ℃ that stretch and be 5MPa～200MPa.
(5). according to (1) described high young's modulus steel plate, it is characterized in that, also contain Ca:0.0005～0.01 quality %.
(6). according to (1) described high young's modulus steel plate, it is characterized in that, also contain among Sn, Co, Zn, W, Zr, V, Mg, the REM more than a kind or 2 kinds, their total content is 0.001～1.0 quality %.
(7). according to (1) described high young's modulus steel plate, it is characterized in that, also contain among Ni, Cu, the Cr more than a kind or 2 kinds, their total content is 0.001～4.0 quality %.
(8). a kind of hot-dip galvanized steel sheet is characterized in that the galvanizing that has (1) described high young's modulus steel plate and apply on described high young's modulus steel plate.
(9). a kind of alloyed hot-dip galvanized steel plate, it is characterized in that, have (1) described high young's modulus steel plate and on described high young's modulus steel plate, apply alloyed hot-dip zinc-coated.
(10). a kind of high Young's modulus steel pipe, it is characterized in that, have (1) described high young's modulus steel plate, and described high young's modulus steel plate is reeled to any direction.
(11). according to the manufacture method of (1) described high young's modulus steel plate, it is characterized in that, have slab is heated to temperature more than 950 ℃ is made hot-rolled steel sheet to implement hot rolling operation, described slab in quality % contain C:0.0005～0.30%, below the Si:2.5%, Mn:2.7～5.0%, below the P:0.15%, below the S:0.015%, Mo:0.15～1.5%, B:0.0006～0.01%, below the Al:0.15%, and surplus is made of Fe and unavoidable impurities; Wherein said hot-rolled process carries out under the following conditions: in surpassing 0.2 and to add up to draft be that mode more than 50% is rolled with the frictional coefficient of roll and steel plate below 800 ℃, and in Ar
3Finish hot rolling under the temperature of transformation temperature～750 ℃.
(12). the manufacture method according to (11) described high young's modulus steel plate is characterized in that in described hot-rolled process, the different circumferential speed of implementing 1 passage at least is that the different circumferential speed more than 1% is rolling.
(13). the manufacture method according to (11) described high young's modulus steel plate, it is characterized in that, in described hot-rolled process, use the roller footpath more than 1 to be the roll below the 700mm at least.
(14). according to the manufacture method of (11) described high young's modulus steel plate, it is characterized in that the hot-rolled steel sheet that also has after described hot rolling finished is that 500 ℃～950 ℃ condition is carried out the annealed operation with continuous annealing line or pack annealing to be up to Da Wendu.
(15). the manufacture method according to (11) described high young's modulus steel plate, it is characterized in that, comprise that also the hot-rolled steel sheet after described hot rolling finished is implemented cold rolling operation to be lower than 60% draft, and after described cold rolling process, carry out the annealed operation.
(16). the manufacture method according to (11) described high young's modulus steel plate is characterized in that also having: described hot-rolled steel sheet is implemented cold rolling operation to be lower than 60% draft; Behind described cold rolling process, be that 500 ℃～950 ℃ condition is carried out the annealed operation to be up to Da Wendu; And below described annealing operation postcooling to 550 ℃, then in 150～550 ℃ of operations of heat-treating.
(17). a kind of manufacture method of hot-dip galvanized steel sheet is characterized in that having: the operation of the high young's modulus steel plate of having annealed by the manufacture method manufacturing of (14) described high young's modulus steel plate; And the operation of described high young's modulus steel plate being implemented galvanizing.
(18). a kind of manufacture method of alloyed hot-dip galvanized steel plate is characterized in that having: the operation of making hot-dip galvanized steel sheet by the manufacture method of (17) described hot-dip galvanized steel sheet; And described hot-dip galvanized steel sheet carried out heat treated operation more than 10 seconds 450～600 ℃ temperature range.
(19). a kind of manufacture method of hot-dip galvanized steel sheet is characterized in that having: the operation of the high young's modulus steel plate of having annealed by the manufacture method manufacturing of (15) described high young's modulus steel plate; And the operation of described high young's modulus steel plate being implemented galvanizing.
(20). a kind of manufacture method of alloyed hot-dip galvanized steel plate is characterized in that having: the operation of making hot-dip galvanized steel sheet by the manufacture method of (19) described hot-dip galvanized steel sheet; And described hot-dip galvanized steel sheet carried out heat treated operation more than 10 seconds 450～600 ℃ temperature range.
(21). a kind of manufacture method of high Young's modulus steel pipe is characterized in that having: the operation of making high young's modulus steel plate by the manufacture method of (11) described high young's modulus steel plate; With described high young's modulus steel plate is reeled and is made steel pipe to any direction.
(22). a kind of high young's modulus steel plate, it is characterized in that, in quality % contain C:0.0005～0.30%, below the Si:2.5%, Mn:0.1～5.0%, below the P:0.15%, below the S:0.015%, below the Al:0.15%, below the N:0.01%; And contain in Mo:0.005～1.5%, Nb:0.005～0.20%, Ti:48/14 * N (quality %)～0.2%, B:0.0001～0.01% more than a kind or 2 kinds, add up to 0.015～1.91 quality %; And surplus is made of Fe and unavoidable impurities; Wherein, 1/8 layer of thickness of slab 110}＜223〉and/or 110}＜111〉and utmost point density be more than 10, the Young's modulus of rolling direction surpasses 230GPa.
(23). according to (22) described high young's modulus steel plate, it is characterized in that, contain whole described Mo, Nb, Ti, B, their content is respectively Mo:0.15～1.5%, Nb:0.01～0.20%, Ti:48/14 * N (quality %)～0.2%, B:0.0006～0.01%, and 1/8 layer of thickness of slab 110}＜001〉utmost point density be below 3.
(24). according to (22) described high young's modulus steel plate, it is characterized in that, 1/8 layer of described thickness of slab 110}＜001〉and utmost point density be below 6.
(25). according to (22) described high young's modulus steel plate, it is characterized in that, is being that the Young's modulus of 1/8 layer rolling direction is more than the 240GPa apart from the top layer of thickness of slab at least.
(26). according to (22) described high young's modulus steel plate, it is characterized in that, 1/2 layer of thickness of slab 211}＜011〉and utmost point density be more than 6.
(27). according to (22) described high young's modulus steel plate, it is characterized in that, 1/2 layer of thickness of slab 332}＜113〉and utmost point density be more than 6.
(28). according to (22) described high young's modulus steel plate, it is characterized in that, 1/2 layer of thickness of slab 100}＜011〉and utmost point density be below 6.
(29). according to (22) described high young's modulus steel plate, it is characterized in that deducting the BH amount that the difference of the flow stress that stretched estimates at 2% o'clock by the upper yield point of 2% back when implementing thermal treatments in 20 minutes and carrying out tension test once again for 170 ℃ that stretch is 5MPa～200MPa.
(30). according to (22) described high young's modulus steel plate, it is characterized in that, also contain Ca:0.0005～0.01 quality %.
(31). according to (22) described high young's modulus steel plate, it is characterized in that, also contain among Sn, Co, Zn, W, Zr, V, Mg, the REM more than a kind or 2 kinds, their total content is 0.001～1.0 quality %.
(32). according to (22) described high young's modulus steel plate, it is characterized in that, also contain among Ni, Cu, the Cr more than a kind or 2 kinds, their total content is 0.001～4.0 quality %.
(33). a kind of hot-dip galvanized steel sheet, it is characterized in that having (22) described high young's modulus steel plate, and the galvanizing that on described high young's modulus steel plate, applies.
(34). a kind of alloyed hot-dip galvanized steel plate, it is characterized in that, have (22) described high young's modulus steel plate and on described high young's modulus steel plate, apply alloyed hot-dip zinc-coated.
(35). a kind of high Young's modulus steel pipe is characterized in that having (22) described high young's modulus steel plate and described high young's modulus steel plate and reel to any direction.
(36). according to the manufacture method of (22) described high young's modulus steel plate, it is characterized in that, have slab be heated to temperature more than 1000 ℃ is made hot-rolled steel sheet to implement hot rolling operation, described slab in quality % contain C:0.0005～0.30%, below the Si:2.5%, Mn:0.1～5.0%, below the P:0.15%, below the S:0.015%, below the Al:0.15%, below the N:0.01%; And contain in Mo:0.005～1.5%, Nb:0.005～0.20%, Ti:48/14 * N (quality %)～0.2%, B:0.0001～0.01% more than a kind or 2 kinds, add up to 0.015～1.91 quality %; And surplus is made of Fe and unavoidable impurities; Wherein said hot-rolled process carries out under the following conditions: the Effective strain amount ε that surpasses 0.2, calculated by following formula [1] with the frictional coefficient of roll and steel plate
*Be more than 0.4 and to add up to draft be that mode more than 50% is rolled, and in Ar
3Finish hot rolling under the temperature of transformation temperature～900 ℃,
N is finish rolling hot rolled rolling machine frame number, ε in the formula
jBe strain, the ε that the j frame applies
nBe strain, the t that the n frame applies
iBe working time (second), the τ between i frame～i+1 frame
iCan be by the rolling temperature T of gas law constant R (=1.987) with the i frame
i(K) calculate by following formula [2],
T
i＝8.46×10
-9×exp{43800/R/T
i} [2]。
(37). the manufacture method according to (36) described high young's modulus steel plate is characterized in that in described hot-rolled process, the different circumferential speed that applies the above different circumferential speed of 1 passage at least and be more than 1% is rolling.
(38). the manufacture method according to (36) described high young's modulus steel plate, it is characterized in that, in described hot-rolled process, use the roller footpath more than 1 to be the roll below the 700mm at least.
(39). according to the manufacture method of (36) described high young's modulus steel plate, it is characterized in that the hot-rolled steel sheet that also has after described hot rolling finished is that 500 ℃～950 ℃ condition is carried out the annealed operation with continuous annealing line or pack annealing to be up to Da Wendu.
(40). the manufacture method according to (36) described high young's modulus steel plate, it is characterized in that, comprise that also the hot-rolled steel sheet after described hot rolling finished is implemented cold rolling operation to be lower than 60% draft, and after described cold rolling process, carry out the annealed operation.
(41). the manufacture method according to (36) described high young's modulus steel plate is characterized in that also having: described hot-rolled steel sheet is implemented cold rolling operation to be lower than 60% draft; After described cold rolling process, be that 500 ℃～950 ℃ condition is carried out the annealed operation to be up to Da Wendu; And below described annealing operation postcooling to 550 ℃, then in 150～550 ℃ of operations of heat-treating.
(42). a kind of manufacture method of hot-dip galvanized steel sheet, it is characterized in that, have: the operation of the high young's modulus steel plate of having annealed by the manufacture method manufacturing of (39) described high young's modulus steel plate, and the operation of described high young's modulus steel plate being implemented galvanizing.
(43). a kind of manufacture method of alloyed hot-dip galvanized steel plate, it is characterized in that, have: the manufacture method by (42) described hot-dip galvanized steel sheet is made the operation of hot-dip galvanized steel sheet, and to described hot-dip galvanized steel sheet 450～600 ℃ of heat treated operations of implementing more than 10 seconds.
(44). a kind of manufacture method of hot-dip galvanized steel sheet, it is characterized in that, have: the operation of the high young's modulus steel plate of having annealed by the manufacture method manufacturing of (40) described high young's modulus steel plate, and the operation of described high young's modulus steel plate being implemented galvanizing.
(45). a kind of manufacture method of alloyed hot-dip galvanized steel plate, it is characterized in that, have: the manufacture method by (44) described hot-dip galvanized steel sheet is made the operation of hot-dip galvanized steel sheet, and to described hot-dip galvanized steel sheet 450～600 ℃ of heat treated operations of implementing more than 10 seconds.
(46). a kind of manufacture method of high Young's modulus steel pipe, it is characterized in that, have: make the operation of high young's modulus steel plate and described high young's modulus steel plate is made steel pipe to any direction coiling by the manufacture method of (36) described high young's modulus steel plate.
According to high young's modulus steel plate of the present invention, above-mentioned by being defined as (1) or (22) described composition, near the shearing texture prosperity low temperature γ district can make the top layer.And, by forming above-mentioned (1) or (22) described texture, especially can realize the good Young's modulus of rolling direction (RD direction).
According to the manufacture method of high young's modulus steel plate of the present invention, the slab of above-mentioned by using (11) or (36) described composition, near the shearing texture prosperity low temperature γ district can make the top layer.And, by carrying out hot rolling, can make above-mentioned (1) or (22) described texture with above-mentioned condition, especially can access the good steel plate of Young's modulus of rolling direction (RD direction).
Description of drawings
Fig. 1 is the sectional view of the test piece of expression hat pliability test use.
Embodiment
Be defined as reason as described above in the present invention steel being formed and created conditions, be described as follows.
(the 1st embodiment)
The steel plate of the 1st embodiment is, in quality % contain C:0.0005～0.30%, below the Si:2.5%, Mn:2.7～5.0%, below the P:0.15%, below the S:0.015%, Mo:0.15～1.5%, B:0.0006～0.01%, below the Al:0.15%; And surplus is made of Fe and unavoidable impurities.1/8 layer of thickness of slab 110}＜223〉with 110}＜111〉the utmost point density of either party or the two be more than 10, the Young's modulus of rolling direction surpasses 230GPa.
C is the cheap element that tensile strength is increased, and its addition is adjusted according to the target strength level.Be lower than the occasion of 0.0005 quality % at C, not only on the steel-smelting technology difficulty and cost improve, the fatigue characteristic deterioration of weld metal zone.Therefore, lower limit is defined as 0.0005 quality %.On the other hand, in the occasion of C content, cause the deterioration or the infringement weldability of plasticity above 0.30 quality %.Therefore the upper limit is defined as 0.30 quality %.
Si has the effect that the intensity of making increases as the solution strengthening element, comprises that for obtaining organizing of martensite and bainite and remaining γ etc. also is effective in addition.Its addition is adjusted according to the target strength level.Press forming deterioration when addition surpasses 2.5 quality %, and cause the decline of chemical convertibility.Therefore, the upper limit is defined as 2.5 quality %.
Implementing the occasion of galvanizing, because the decline of the adaptation of coating, the delay of alloying reaction produce the problems such as reduction of productivity, so preferably Si is defined as below the 1.2 quality %.Lower limit is not done special setting, but be defined as 0.001 quality % when following manufacturing cost improve, therefore surpassing 0.001 quality % is the lower limit of essence.
Mn is important for the present invention.That is be necessary element, in order to obtain high Young's modulus.For the present invention, near the shearing texture prosperity by making the steel plate top layer in low temperature γ district can make the Young's modulus prosperity of rolling direction (RD direction).Mn expands to cold zone with γ phase stabilization and with the γ district, therefore carries out the low temperature rolling in γ district easily.And has Mn itself plays advantageous effect near the formation of the shearing texture the top layer a possibility.From these viewpoints, the minimum interpolation 2.7 quality % of Mn.On the other hand, intensity too improves when surpassing 5.0 quality %, and ductility reduces or hinders galvanized adaptation.So the upper limit is defined as 5.0 quality %, be preferably 2.9～4.0 quality %.
P is known to be the same element that improves intensity cheaply with Si, in the occasion that requires to gain in strength, adds more energetically.P has the effect with hot rolling microstructure miniaturization, raising processibility.But when addition surpassed 0.15 quality %, the fatigue strength of some postwelding worsens or yield strength too increases, and causes the face shape defect when punching press.And alloying reaction is extremely slow when continuous hot-dipping galvanizing, and productivity reduces.Therefore, its upper limit is defined as 0.15 quality %.
S becomes the reason that produces thermal crack when surpassing 0.015 quality %, processibility is worsened, so the upper limit is defined as 0.015 quality %.
Mo and B: for the present invention is important.By the interpolation of these elements, just may improve the Young's modulus of rolling direction first.Although this reason and not really clear can be thought, because the effect of Mo, B and the compound interpolation of Mn, the crystal that shearing strain caused of frictional force of steel plate and roll of resulting from rotates and changes.Its result forms very sharp-pointed texture on the top layer of hot-rolled sheet near the scope 1/4 layer of the thickness of slab, and the Young's modulus of rolling direction improves.
The lower limit of Mo and B content is respectively Mo:0.15 quality %, B:0.0006 quality %.This is because than its a spot of interpolation.Its above-mentioned Young's modulus improves the less cause of effect.On the other hand, add even Mo and B surpass 1.5 quality % respectively and surpass 0.01 quality %, the saturated and cost of the raising effect of its Young's modulus improves, and therefore 1.5 quality % and 0.01 quality % is defined as their upper limit respectively.
In addition, these elements add the Young's modulus that causes simultaneously and improve effect, encourage more by the combination meeting with C.Therefore, preferably the C amount is defined as more than the 0.015 quality %.
Al also can be used as the deoxidation conditioning agent and uses.But Al significantly improves transformation temperature, so the rolling difficulty that becomes in low temperature γ district, so the upper limit is defined as 0.15 quality %.
In the steel plate of the present embodiment, except above-mentioned composition, preferably also contain Ti, Nb.Ti, Nb have the effect of encouraging above-mentioned Mn, Mo, B and further improving Young's modulus.And, produce effect for the raising of processibility and high strength and to the miniaturization and the homogenizing of tissue, therefore add as requested.But, when being lower than 0.001 quality % respectively, its addition can not see effect, even when surpassing 0.20 quality % on the other hand respectively and adding, it is saturated that its effect also is tending towards, and therefore it is defined as the upper limit.Be preferably 0.015～0.09 quality %.
Ca is useful as deoxidant element, also proves effective for the morphology Control of sulfide in addition, therefore also can add in the scope of 0.0005～0.01 quality %.Effect is insufficient when being lower than 0.0005 quality %, processibility worsens when surpassing 0.01 quality % interpolation, therefore is defined as this scope.
For with they steel plates as principal constituent, also can contain among Sn, Co, Zn, W, Zr, Mg, the REM more than a kind or 2 kinds, add up to 0.001～1.0 quality %.At this, REM represents the rare earth metal element, be from Sc, Y, La, Ce, Pr, Nd, Pm, Sm, Eu, Gd, Tb, Dy, Ho, Er, Tm, Yb, Lu, select more than a kind.
But Zr forms ZrN, so solid solution N minimizing, so preferably be defined as below the 0.01 quality %.
Ni, Cu, Cr are used to carry out the rolling favourable element in low temperature γ district, therefore also can with the scope that adds up to 0.001～4.0 quality % add they more than a kind or 2 kinds.Can not obtain significant effect when being lower than 0.001 quality %, processibility worsens when surpassing 4.0 quality % interpolation.
N: being the γ stabilizing element, is to be used to carry out the rolling favourable element in low temperature γ district therefore.Therefore, also can be at 0.02 quality % with interior interpolation.0.02 quality % is defined as the upper limit of essence, is because being added in the manufacturing more than this is difficult.
Solid solution N and solid solution C amount are preferably 0.0005～0.004 quality % respectively.Strain aging when processed, also can take place as member in steel plate at normal temperatures that contain them, and Young's modulus improves.For example, the occasion of using in the automobile purposes is implemented the coating baking processing by processing the back, and not only the yield strength of steel plate increases, and Young's modulus also improves.
Solid solution N and solid solution C amount also can be tried to achieve from the difference that total C, N amount deducts C, the N amount (chemical analysis according to extraction residue carries out quantitatively) that the compound as Fe, Al, Ti, B etc. exists.And, also can adopt internal friction method and FIM (field-ion microscopy: Field IonMicroscopy) obtain.
When solid solution C and solid solution N amount is lower than 0.0005 quality %, can not obtain effect of sufficient, even and when surpassing 0.004 quality % BH also be tending towards saturated, so the upper limit is defined as 0.004 quality %.
Secondly, texture, Young's modulus and the BH amount with regard to steel plate describes.
The thickness of slab of the steel plate of the 1st embodiment/8 layers 110}＜223〉and/or 110}＜111〉and utmost point density be more than 10.Thus, can improve the Young's modulus of rolling direction.Be lower than 10 occasion in above-mentioned utmost point density, it is difficult that the Young's modulus of rolling direction surpasses 230GPa.Above-mentioned utmost point density is preferably more than 14, more preferably more than 20.
The utmost point density in these orientation (X ray random strength than), according to X-ray diffraction measure 110}, 100}, 211}, the Series Expansion Method that is base with many pole graphs in the 310} pole graph calculate 3 tie up texture (ODF) and obtain and get final product.That is, in order to obtain the utmost point density of each crystal orientation, with the intensity of (110) [2-23] (110) [1-11] of the φ 2=45 ° section of 3 dimension texture as representative.
An example of below representing above-mentioned utmost point density measurement.
According to the following making of carrying out X-ray diffraction with sample like that.
In the thickness of slab direction steel plate is ground to the position of regulation by mechanical mill and chemical grinding etc.After this abrasive surface is finish-machined to minute surface by polishing, eliminate strain deformation, simultaneously 1/8 layer of thickness of slab or 1/2 layer described later are adjusted into the mensuration face by means of electrolytic polishing and chemical grinding.For example,, when the thickness of slab of steel plate is t, grind surface of steel plate with the amount of grinding of the thickness of t/8 1/8 layer occasion, and with the abrasive surface that exposes as the mensuration face.In addition, exactly that 1/8 layer of thickness of slab and 1/2 layer is very difficult as the mensuration face, therefore the destination layer with them is the center, and-3%～+ 3% of thickness of slab scope is made sample as the mensuration face and got final product relatively.In addition, confirm to have the occasion of segregation line, do not have the position of segregation line to measure for 3/8～5/8 scope of thickness of slab and get final product at the thickness of slab central core of steel plate.In addition, measure difficult occasion, adopt EBSP method and ECP method to add up the mensuration of ground quantity sufficient at X ray.
Above-mentioned hkl}＜uvw 〉, mean when taking X ray with sample with aforesaid method with the vertical crystal orientation of plate face for the crystal orientation of the length direction of hkl}, steel plate is＜uvw 〉.
Feature about the texture of steel plate, only then can not represent with common antipole point diagram and positive pole graph, for example about near the occasion of the antipole point diagram of the crystal orientation of the plate face normal direction of measuring the expression steel plate 1/8 layer of thickness of slab, the face strength ratio in each orientation (X ray random strength than) preferably,＜110 〉: more than 5,＜112: more than 2.And, about 1/2 layer, preferably,＜112 〉: more than 4,＜332: more than 1.5.
About the qualification of above-mentioned utmost point density, 1/8 layer with regard to thickness of slab should satisfy at least, but preferred just 1/8 layer of thickness of slab satisfy, also set up up to 1/4 layer wide region from the thickness of slab top layer.For 1/8 layer of thickness of slab, 110}＜001〉and 110}＜110〉existing hardly, their utmost point density preferably is lower than 1.5, more preferably is lower than 1.0.At steel plate in the past, this orientation exists to a certain degree on the top layer, therefore fails to improve the Young's modulus of rolling direction.
In the 1st embodiment, further preferably, 1/2 layer of thickness of slab 112}＜110〉utmost point density of ((112) [1-10] of the φ 2=45 ° section of above-mentioned ODF) is more than 6.If this orientation prosperity, with the vertical width of rolling direction (the following TD direction that also claims)＜111〉orientation assemble, so the Young's modulus of TD direction improves.Be lower than at 6 o'clock in this utmost point density, it is difficult that the Young's modulus of TD direction surpasses 230GPa, therefore it is defined as lower limit.Preferred utmost point density is more than 8, more preferably more than 10.
In addition, 1/2 layer of thickness of slab 554}＜225〉and 332}＜113〉utmost point density of ((554) [-2-25] of the φ 2=45 ° section of above-mentioned ODF and (332) [-1-13]) has been expected some contribution to the Young's modulus of rolling direction, therefore is preferably more than 3.
Above-described crystal orientation all allow surpass-2.5 ° ,+2.5 ° with interior scattered error fluctuation.
The important document of the utmost point density of the crystal orientation by satisfying relevant 1/8 layer of above-mentioned thickness of slab and 1/2 layer simultaneously, the two Young's modulus of rolling direction and TD direction is possible above 230GPa simultaneously.
The steel plate of the 1st embodiment surpasses 230GPa in the Young's modulus of rolling direction.The mensuration of this Young's modulus is the high temperature Young's modulus measuring method according to the JISZ2280 of Japanese Industrial Standards metallic substance, adopts the lateral resonance method to carry out at normal temperatures.That is, material is fixed, under quick condition, this sample is applied vibration by the vibrator of outside, the vibrational frequency of this vibrator is slowly changed, measure the first resonance frequency of said sample, calculate Young's modulus by following formula [3] in transverse vibration.
E＝0.946×(1/h)
3×m/w×f
2 [3]
In the formula, E: kinetic Young's modulus (N/m
2), 1: the length of test piece (m), h: the thickness of test piece (m), m: quality (kg), w: the width of test piece (m), f: the first resonance frequency (sec of lateral resonance method
-1).
The BH amount of steel plate is preferably more than the 5MPa.That is, this is that the Young's modulus of actual measurement improves when because of handling by means of coating baking mobile dislocation being fixed.When the BH amount was lower than 5MPa, its effect lacked.Also can't see especially effect even surpass 200MPa.Therefore, the scope with the BH amount is defined as 5～200MPa.This BH amount is 30～100MPa more preferably.
So-called BH amount, the flow stress that steel plate stretched 2% o'clock is σ
2(MPa), behind the steel plate drawn 2% again the upper yield point when 170 ℃ are implemented that thermal treatment stretched once again in 20 minutes be σ
1(MPa) time, represent by following formula [4].
BH＝σ
1—σ
2(MPa) [4]
It is that coating and various plating are also passable that above-mentioned hot-rolled steel sheet, cold-rolled steel sheet are implemented Al.Implement the steel plate of various coating to hot-rolled steel sheet and cold-rolled steel sheet and to them, can carry out the surface treatment of organic epithelium, inorganic epithelium and various coating etc. according to purpose.
Secondly, the manufacture method with regard to the steel plate of the 1st embodiment is described.
In the 1st embodiment, have slab is heated to that temperature more than 950 ℃ is implemented hot rolling and the operation of making hot-rolled sheet, wherein said slab in quality % contain C:0.0005～0.30%, below the Si:2.5%, Mn:2.7～5.0%, below the P:0.15%, below the S:0.015%, Mo:0.15～1.5%, B:0.0006～0.01%, below the Al:0.15%, and surplus is made of Fe and unavoidable impurities.
Supply with this hot rolled slab, be not particularly limited.That is be to get final product, by the slab that continuous casting steel billet and thin slab casting machine etc. are made.And, after casting, carry out the such technology of hot rolled continuous casting-directly rolling (CC-DR) immediately and also be fit to.
In the occasion of hot-rolled steel sheet as the finished product, it is necessary limiting following such creating conditions.
The hot rolling Heating temperature is more than 950 ℃.This is because hot rolling finishing temperature described later is defined as Ar
3It more than the transformation temperature necessary temperature.
So that the mode that adds up to more than 50% of the draft of each passage below 800 ℃ is carried out hot rolling.This moment, the frictional coefficient of roll and steel plate surpassed 0.2.This is the shearing texture prosperity that makes the top layer, the necessary condition that improves the Young's modulus of rolling direction.
The total of draft is preferably more than 70%, more preferably more than 100%.The total of so-called draft, in the rolling occasion of n passage, each draft of establishing the 1st passage～n passage is respectively R1 (%)～Rn (%), then is defined as R1+R2+ ... + Rn.Thickness of slab after thickness of slab-n passage after Rn={ (n-1) passage }/thickness of slab * 100% after (n-1) passage.
The hot rolled finishing temperature is Ar
3More than the transformation temperature, below 750 ℃.Be lower than Ar
3During transformation temperature, to the Young's modulus of rolling direction preferred 110}＜001〉the texture prosperity.And, when finishing temperature surpasses 750 ℃, make near 1/4 layer from the thickness of slab top layer to thickness of slab that preferred texture prosperity is difficult to rolling direction.
Coiling temperature after rolling is not particularly limited, and some occasion Young's modulus improves when batching for 400～600 ℃, therefore preferably batches in this scope.
When implementing hot rolling, the different circumferential speed of preferably implementing the above roll of 1 passage at least is that the different circumferential speed more than 1% is rolling.Thus, promote that near the texture the top layer forms, therefore the occasion rolling with not implementing different circumferential speed compared, and Young's modulus is improved.According to this viewpoint, preferably be defined as different circumferential speed more than 1%, more preferably more than 5%, most preferably be that to carry out different circumferential speed more than 10% rolling comparatively desirable.
The upper limit of the road number of times that different circumferential speed and different circumferential speed are rolling is not done special stipulation, but undoubtedly, and from above-mentioned reason as can be seen, their all big persons can obtain bigger Young's modulus and improve effect.But the different circumferential speed more than 50% is difficult at present, and the passage of hot finishing is generally about 8 passages.
At this, so-called different circumferential speed of the present invention will be represented to obtain with percentage divided by the value of the circumferential speed of low speed side roll by the difference of the circumferential speed of top and bottom rolls.In addition, different circumferential speed of the present invention is rolling, and no matter which side is big for the circumferential speed of top and bottom rolls, and Young's modulus is improved effect does not all have difference.
In the milling train that hot finishing is used, preferably use the roller diameter more than 1 to be the working roll below the 700mm.Thus, can promote near the formation of the texture that the top layer is, therefore compare, Young's modulus is further improved with obsolete occasion.From this viewpoint, with work roll diameter be defined as below the 700mm, be preferably below the 600mm, more preferably below the 500mm.The lower limit of work roll diameter does not have special stipulation, but for 300mm when following logical plate control become difficult.Use the upper limit of the passage of minor diameter roller not have special stipulation, such as described above, the hot finishing passage is generally about 8 passages.
With the hot-rolled steel sheet of making like this, it is preferred being up to the thermal treatment that Da Wendu is 500～950 ℃ a scope (annealing) after pickling.Thus, the Young's modulus of rolling direction further improves.Although this reason determines as yet, by inference, be since the dislocation that the phase transformation after rolling is introduced through due to Overheating Treatment arranges once more.
When being up to Da Wendu and being lower than 500 ℃, its effect is not remarkable, on the other hand, α → γ phase transformation takes place when surpassing 950 ℃, and therefore consequently, the gathering of texture is identical or die down, and Young's modulus also is the tendency of deterioration.Therefore, be defined as the lower limit and the upper limit respectively with 500 ℃ and 950 ℃.
This scope that is up to Da Wendu is preferably 650 ℃～850 ℃.This heat treating method is not particularly limited, and gets final product in common continuous annealing line and pack annealing and continuous hot-dipping zinc wire described later.
Implement cold rolling and thermal treatment (annealing) is also passable to hot-rolled steel sheet.Cold rolling rate is for being lower than 60%.This is because if cold rolling rate is more than 60%, and the texture of the raising Young's modulus that then forms in hot-rolled steel sheet can great changes have taken place, and the Young's modulus of rolling direction reduces.
Implement thermal treatment in cold rolling end back.This heat treated Da Wendu of being up to is 500～950 ℃ a scope.Young's modulus raising degree reduces when being lower than 500 ℃, and some occasion processibility deterioration, therefore is defined as lower limit with 500 ℃.
On the other hand, when thermal treatment temp surpasses 950 ℃, α → γ phase transformation takes place, therefore consequently, the gathering of texture is identical or die down, and Young's modulus also is the tendency of deterioration.Therefore, be defined as the lower limit and the upper limit respectively with 500 ℃ and 950 ℃.This preferable range that is up to Da Wendu is 600 ℃～850 ℃.
After the above-mentioned thermal treatment, carry out once up to 550 ℃, be preferably up to the cooling below 450 ℃, to implement thermal treatments in 150～550 ℃ more also be possible.These various purposes such as organizational controls according to the promotion of the phase transformation of the control of solid solution C amount and martensitic tempering, bainite etc. select suitable condition to get final product.
The tissue of the steel plate that obtains according to the manufacture method of the high young's modulus steel plate of the present embodiment, with ferrite or bainite as principal phase, two-phase mix to exist also can, having martensite, austenite, carbide, nitride in the tissue is that main compound is also passable.That is, characteristic is made tissue respectively and is got final product as requested.
(the 2nd embodiment)
The steel plate of the 2nd embodiment is, in quality % contain C:0.0005～0.30%, below the Si:2.5%, Mn:0.1～5.0%, below the P:0.15%, below the S:0.015%, below the Al:0.15%, below the N:0.01%; And contain in Mo:0.005～1.5%, Nb:0.005～0.20%, Ti:48/14 * N (quality %)～0.2%, B:0.0001～0.01% more than a kind or 2 kinds, add up to 0.015～1.91 quality %; And surplus is made of Fe and unavoidable impurities.1/8 layer of thickness of slab 110}＜223〉and/or 110}＜111〉and utmost point density be more than 10, the Young's modulus of rolling direction surpasses 230GPa.
At this, describe with regard to the above-mentioned reason that limits the steel composition like that.
C is the element that tensile strength is increased, and its addition is adjusted according to the target strength level.When C is lower than 0.0005 quality % not only on the steel-smelting technology difficulty and cost improve but also the fatigue characteristic deterioration of weld metal zone.Therefore, lower limit is defined as 0.0005 quality %.On the other hand, when C content surpasses 0.30 quality %, cause the deterioration or the infringement weldability of plasticity, so the upper limit is defined as 0.30 quality %.
Si has the effect that the intensity of making increases as the solution strengthening element, comprises that for obtaining organizing of martensite and bainite and remaining γ etc. also is effective in addition.Its addition is adjusted according to the target strength level.Press forming deterioration when addition surpasses 2.5 quality %, and cause the decline of chemical convertibility.Therefore, the upper limit is defined as 2.5 quality %.And implementing the occasion of galvanizing, because the decline of the adaptation of coating, the delay of alloying reaction produce the problems such as reduction of productivity, so preferably Si is defined as below the 1.2 quality %.Though lower limit is not set especially, be defined as 0.001 quality % its manufacturing cost raising when following, so this is the lower limit of essence.
Mn expands to cold zone with γ phase stabilization and with the γ district, therefore carries out the low temperature rolling in γ district easily.And has Mn itself plays advantageous effect near the formation of the shearing texture the top layer a possibility.From these viewpoints, the addition of Mn is preferably more than the 0.1 quality %, more preferably more than the 0.5 quality %, more preferably more than the 1.5 quality %.On the other hand, when surpassing 5.0 quality %, intensity too improves, and ductility reduces, hinders galvanized adaptation, therefore with 0.5 quality % as the upper limit.Thus, the addition of Mn is preferably 2.9～4.0 quality %.
P is known to be the same element that improves intensity cheaply with Si, in the occasion that requires to gain in strength, adds more energetically.In addition, P also has the effect with hot rolling microstructure miniaturization, raising processibility.But when addition surpassed 0.15 quality %, the fatigue strength of some postwelding worsened, yield strength too increases, and caused the face shape defect when punching press.And alloying reaction is extremely slow when continuous hot-dipping galvanizing, and productivity reduces, and also deterioration of 2 processibilities.Therefore, its upper limit is defined as 0.15 quality %.
S becomes the reason that produces hot-rolled crackle when surpassing 0.015 quality %, processibility is worsened, so the upper limit is defined as 0.015 quality %.
Mo, Nb, Ti and B are important for the present invention.By adding more than a kind or 2 kinds of these elements, just may improve the Young's modulus of rolling direction first.Although this reason and not really clear, the sharpening of the processing texture by suppressing recrystallize in the hot rolling and γ phase, the result results from the shearing strain texture of steel plate and roll and also changes.Scope till 1/4 layer forms very sharp-pointed texture from the top layer of hot-rolled sheet to thickness of slab thus, and the Young's modulus of rolling direction improves.
The lower limit of Mo, Nb, Ti and B content is respectively 0.005 quality %, 0.005 quality %, 48/14 * N quality % and 0.0001 quality %; Preferably be respectively 0.03 quality %, 0.01 quality %, 0.03 quality % and 0.0003 quality %; More preferably be respectively 0.1 quality %, 0.03 quality %, 0.05 quality % and 0.0006 quality %.This is because than its a spot of interpolation, the cause that the effect of above-mentioned raising Young's modulus becomes very little.
On the other hand, even Mo, Nb, Ti and B surpass 1.5 quality % respectively, surpass 0.2 quality %, surpass 0.2 quality % and surpass 0.01 quality % and add, saturated and the cost of the raising effect of its Young's modulus improves, therefore with 1.5 quality %, 0.2 quality %, 0.2 quality % and 0.01 quality % respectively as the upper limit of the addition of Mo, Nb, Ti and B.
And the addition of the total of these elements can not obtain sufficient Young's modulus and improve effect when being lower than 0.015 quality %, and therefore the lower limit with the addition that adds up to is defined as 0.015 quality %.From this viewpoint, preferably adding up to addition is more than the 0.035 quality %, and preferred total addition is more than the 0.05 quality %.Add up to the upper limit of addition to be defined as the upper limit sum of addition separately, i.e. 1.91 quality %.
Exist between Mo, Nb, Ti and the B to interact, strengthen more by its texture of compound interpolation, Young's modulus raises.Thus, compound interpolation is even more ideal more than at least 2 kinds.Especially Ti forms nitride in γ high-temperature zone and N, can suppress the generation of BN.Therefore, in the occasion of adding B, Ti also preferably adds more than 48/14 * N quality %.
And, contain all that Mo, Nb, Ti and B, element separately preferably add 0.15 quality %, 0.01 quality %, 48/14 * N quality % respectively and more than the 0.0006 quality %.In this occasion, the texture sharpening, particularly make top layer that Young's modulus lowers 110}＜001〉reduce, Young's modulus rises effectively.Therefore, can reach the high Young's modulus of L direction.
In addition, these elements add the Young's modulus that causes simultaneously and improve effect and encouraged more by the combination meeting with C.Therefore, preferably the C amount is defined as more than the 0.015 quality %.
The lower limit of Mo, Nb and B content is respectively 0.15 quality %, 0.01 quality % and 0.0006 quality %.This is because than its a spot of interpolation the time, and above-mentioned Young's modulus improves effect and can reduce.But, in the occasion of the Young's modulus of only controlling the top layer,, can obtain sufficient Young's modulus and improve effect if add the above Mo of 0.1 quality %, therefore it is defined as lower limit.On the other hand, when Mo, Nb and B surpass 1.5 quality % respectively, surpass 0.2 quality % and surpass 0.01 quality % interpolation, Young's modulus improves the saturated and cost of effect and improves, and therefore respectively 1.5 quality %, 0.2 quality % and 0.01 quality % is defined as their upper limit.
In addition, these elements add the Young's modulus that causes simultaneously and improve effect and encouraged more by the combination meeting with C.Therefore, preferably the C amount is defined as more than the 0.015 quality %.
Al also can be used as the deoxidation conditioning agent and uses.But Al significantly improves transformation temperature, so the rolling difficulty that becomes in low temperature γ district, so the upper limit is defined as 0.15 quality %.The lower limit of Al is not particularly limited, but from the viewpoint of deoxidation, preferably is defined as more than the 0.01 quality %.
N and B form nitride, and the inhibition recrystallize effect of B is lowered, and therefore are controlled at below the 0.01 quality %.From this viewpoint, be preferably below the 0.005 quality %, more preferably below the 0.002 quality %.The lower limit of N is not done special setting, but when being lower than 0.0005 quality %, not only spends cost, and does not almost have effect, therefore preferably is defined as more than the 0.0005 quality %.
Solid solution C amount preferably is defined as counting 0.0005～0.004% with quality %.Even also produce strain aging when the steel plate of solid solution C is processed to member at normal temperatures, Young's modulus improves.For example in the occasion that is used for the automobile purposes, the processing back is by implementing coating baking, and not only the yield strength of steel plate improves, and Young's modulus also increases.Solid solution C amount also can be tried to achieve from the difference that total C amount deducts the C amount (chemical analysis according to extraction residue carries out quantitatively) that the compound as Fe, Al, Nb, Ti, B etc. exists.And, also can adopt internal friction method and FIM (field-ion microscopy: Field IonMicroscopy) obtain.
When solid solution C amount is lower than 0.0005 quality %, can not obtain effect of sufficient, even and when surpassing 0.004 quality % BH also be tending towards saturated, so the upper limit is defined as 0.004 quality %.
At the steel plate of the 2nd embodiment, except above-mentioned composition, also preferably contain Ca:0.0005～0.01 quality % in quality %.
Ca is useful as deoxidant element, also proves effective for the morphology Control of sulfide in addition, therefore also can add in the scope of 0.0005～0.01 quality %.Effect is insufficient when being lower than 0.0005 quality %, processibility worsens when surpassing 0.01 quality % interpolation, therefore is defined as this scope.
Also can in quality % contain among Sn, Co, Zn, W, Zr, V, Mg, the REM more than a kind or 2 kinds, add up to 0.001～1.0 quality %.Special W and V have the recrystallize effect that suppresses the γ district, therefore preferably add respectively more than the 0.01 quality %.But Zr forms ZrN, so solid solution N minimizing, so preferably be defined as below the 0.01 quality %.
In addition, also can in quality % contain among Ni, Cu, the Cr more than a kind or 2 kinds, add up to 0.001～4.0 quality %.
The total of Ni, Cu, Cr addition separately when being lower than 0.001 quality %, can not obtain significant effect, processibility deterioration when surpassing 4.0 quality % interpolation.
Secondly, texture, Young's modulus and the BH amount with regard to steel plate describes.
About the texture of the steel plate of the 2nd embodiment, thickness of slab/8 layers 110}＜223〉and/or 110}＜111〉and utmost point density be more than 10.Thus, may improve the Young's modulus of rolling direction.Be lower than 10 occasion in above-mentioned utmost point density, it is difficult that the Young's modulus desire of rolling direction surpasses 230GPa.Above-mentioned utmost point density is preferably more than 14, more preferably more than 20.
The utmost point density in these orientation (X ray random strength than) according to X-ray diffraction measure 110}, 100}, 211}, the Series Expansion Method that is base with many pole graphs in the 310} pole graph calculate 3 tie up texture (ODF) and obtain and get final product.That is, in order to obtain the utmost point density of each crystal orientation, with the intensity of (110) [2-23] (110) [1-11] of the φ 2=45 ° section of 3 dimension texture as representative.
The mensuration of this utmost point density can be suitable for the described method of the 1st embodiment.
About the qualification of above-mentioned utmost point density, satisfy for 1/8 layer of thickness of slab at least, in fact not only 1/8 layer, preferably the wide region till the thickness of slab top layer to 1/4 layer is set up.
In the 2nd embodiment, further preferably, 1/8 layer of thickness of slab 110}＜001〉utmost point density in ((110) [001] of the φ 2=45 ° section of above-mentioned ODF) orientation is below 3.This orientation significantly reduces the Young's modulus of rolling direction, thus this orientation Young's modulus of surpassing 3 o'clock rolling direction to surpass 230GPa be difficult, if consider this point, be preferably below 3, more preferably be lower than 1.5.
1/2 layer of thickness of slab 211}＜011〉utmost point density of ((112) [1-10] of the φ 2=45 ° section of above-mentioned ODF) is preferably more than 6.If this orientation prosperity assemble with the vertical width of rolling direction (RD direction) (TD direction)＜111〉orientation, so the Young's modulus of TD direction improves.Be lower than at 6 o'clock in this utmost point density, it is difficult that the Young's modulus of TD direction surpasses 230GPa, therefore it is defined as lower limit.The preferable range of this utmost point density is more than 8, and preferred scope is more than 10.
1/2 layer of thickness of slab 332}＜113〉and 332}＜113〉and the utmost point density of ((332) [-1-13] of the φ 2=45 ° section of above-mentioned ODF) has been expected some contribution to the Young's modulus of rolling direction, therefore 1/2 layer of this thickness of slab 332}＜113〉and utmost point density be preferably more than 6, more preferably more than 8, more preferably more than 10.
In addition, 1/2 layer of thickness of slab 100}＜011〉utmost point density of ((001) [1-10] of the φ 2=45 ° section of above-mentioned ODF) significantly reduces the Young's modulus of 45 ° of directions, so this utmost point density preferably is defined as below 6.The utmost point density in this orientation more preferably below 3, most preferably is below 1.5.
Above-described crystal orientation all allow surpass-2.5 ° ,+2.5 ° scope is with interior scattered error fluctuation.
Feature about the texture of steel plate, only then can not represent with common antipole point diagram and positive pole graph, for example about near the occasion of the antipole point diagram of the crystal orientation of the plate face normal direction of measuring the expression steel plate 1/8 layer of thickness of slab, the face strength ratio in each orientation (X ray random strength than) is preferably＜and 110 〉: more than 5,＜112: more than 2.And, about 1/2 layer, be preferably＜112: more than 4,＜332: more than 4,＜100: below 3.
Young's modulus about steel plate, by satisfying the important document of 1/8 layer of the above-mentioned thickness of slab and the utmost point density of 1/2 layer relevant crystal orientation simultaneously, not only rolling direction (RD direction) and also with the vertical direction of rolling direction be that to surpass 230GPa simultaneously be possible for the Young's modulus of width (TD direction).The mensuration of Young's modulus is suitable for the described method of the 1st embodiment.
The lower value of the Young's modulus of the rolling direction from the top layer to 1/8 of thickness of slab layer is preferably more than the 240GPa.Thus, can obtain the effect of improving of sufficient shape freezing.The lower value of the Young's modulus of the rolling direction from this top layer to 1/8 layer is 245GPa more preferably, most preferably is 250GPa.Higher limit is not particularly limited, but in order to surpass 300GPa, other alloying element of heavy addition is necessary, and processing waits other deterioration in characteristics, so be essentially below the 300GPa.Even the top layer Young's modulus surpasses 240GPa, its bed thickness is being lower than the effect that can not bring into play the freezing property of abundant raising shape at 1/8 o'clock.Undoubtedly, the thickness of layer with high Young's modulus is thick more, just can obtain high flexural rigidity more.
In addition, the mensuration of the Young's modulus on top layer is to be that thickness more than 1/8 cuts test piece with the distance top layer, carries out according to above-mentioned transverse vibration method.
The top layer Young's modulus of plate width direction does not have special stipulation, undoubtedly, the high person of top layer Young's modulus of plate width direction, the flexural rigidity of its width improves.Contain all above-mentioned Mo, Nb, Ti, B, their content is respectively the composition of Mo:0.15～1.5%, Nb:0.01～0.20%, Ti:48/14 * N (quality %)～0.2%, B:0.0006～0.01%, and by make 1/8 layer of thickness of slab 110}＜223〉and/or 110}＜111〉and utmost point density be more than 10 and also 1/8 layer 110}＜001〉and utmost point density be texture below 3, the also the same 240GPa that surpasses of the top layer Young's modulus of width then with rolling direction.
The BH amount of steel plate is preferably more than the 5MPa.That is, this is because as if handling by means of coating baking and mobile dislocation being fixed, then the Young's modulus of rolling direction (RD direction) improves.When BH amount was lower than 5MPa, its effect lacked, even and surpass 200MPa and also can't see especially effect.Therefore, the BH amount is defined as 5～200MPa.The preferred scope of this BH amount is 30～100MPa.
The BH amount is represented by the described formula of the 1st embodiment [4].
Secondly, described with regard to the manufacture method of the steel plate of the 2nd embodiment.
In the 2nd embodiment, have the temperature that slab is heated to more than 1000 ℃ and implement the operation that hot-rolled sheet is made in hot rolling, wherein said slab in quality % contain C:0.0005～0.30%, below the Si:2.5%, Mn:0.1～5.0%, below the P:0.15%, below the S:0.015%, Mo:0.15～1.5%, B:0.0006～0.01%, below the Al:0.15%, Nb:0.01～0.20%, below the N:0.01%, Ti:48/14 * N (quality %)～0.2%, and surplus is made of Fe and unavoidable impurities.
Supply with this hot rolled slab, be not particularly limited.That is be to get final product, by the slab that continuous casting steel billet and thin slab casting machine etc. are made.And, after casting, carry out the such technology of hot rolled continuous casting-directly rolling (CC-DR) immediately and also be fit to.
In this hot-rolled process, the hot rolling Heating temperature is more than 1000 ℃.The hot rolling Heating temperature is more than 1000 ℃, and this is because hot rolling finishing temperature described later is defined as Ar
3It more than the transformation temperature necessary temperature.
Adopt that the frictional coefficient of roll and steel plate surpasses 0.2, the Effective strain amount ε of following formula [5] calculating
*Be more than 0.4 and to add up to draft be that condition 50% or more is carried out hot rolling, above condition is the necessary condition for the Young's modulus of the shearing texture prosperity that is used to make the top layer, raising rolling direction.
N is finish rolling hot rolled rolling machine frame number, ε in the formula
jBe strain, the ε that the j frame applies
nBe strain, the t that the n frame applies
iBe working time (second), the τ between i frame～i+1 frame
iCan be by means of the rolling temperature T of gas law constant R (=1.987) with the i frame
i(K) calculate by following formula (6).
τ
i＝8.46×10
-9×exp{43800/R/T
i} [6]
The total RT of above-mentioned draft, in the rolling occasion of n passage, each draft of establishing the 1st passage～n passage is respectively R1 (%)～Rn (%), then can be calculated by following formula [7].
RT＝R1+R2+……+Rn [7]
In the formula, the thickness of slab after the thickness of slab-n passage after Rn={ (n-1) passage }/thickness of slab * 100% after (n-1) passage.
Above-mentioned Effective strain amount ε
*Be more than 0.4, be preferably more than 0.5, more preferably more than 0.6.Adding up to more than 50% of above-mentioned draft is preferably more than 70%, more preferably more than 100%.
This hot rolled finishing temperature is Ar
3More than the transformation temperature, below 900 ℃.
Be lower than Ar in finishing temperature
3During transformation temperature, to the Young's modulus of rolling direction preferred 110}＜001〉the texture prosperity.And when finishing temperature surpassed 900 ℃, it was difficult making near 1/4 layer from the thickness of slab top layer to thickness of slab rolling direction is preferably sheared the texture prosperity.From this viewpoint, the hot rolled finishing temperature is preferably below 850 ℃, more preferably below 800 ℃.
Coiling temperature after rolling is not particularly limited, and some occasion Young's modulus improves when batching for 400～600 ℃, therefore preferably batches in this scope.
When implementing hot rolling, the different circumferential speed of preferably implementing the above roll of 1 passage at least is that the different circumferential speed more than 1% is rolling.Thus, promote that near the texture the top layer forms, therefore the occasion rolling with not implementing different circumferential speed compared, and Young's modulus is improved.According to this viewpoint, preferably be defined as different circumferential speed more than 1%, more preferably more than 5, most preferably be that to carry out different circumferential speed more than 10% rolling comparatively desirable.
The upper limit of the road number of times that different circumferential speed and different circumferential speed are rolling is not done special stipulation, but undoubtedly, and from above-mentioned reason as can be seen, their all big persons can obtain bigger Young's modulus and improve effect.But the different circumferential speed more than 50% is difficult at present, and the passage of hot finishing is generally about 8 passages.
At this, so-called different circumferential speed of the present invention will be represented to obtain with percentage divided by the value of the circumferential speed of low speed side roll by the difference of the circumferential speed of top and bottom rolls.Different circumferential speed of the present invention is rolling, and no matter which side is big for the circumferential speed of top and bottom rolls, and Young's modulus is improved effect does not all have difference.
In addition, the milling train of hot finishing use preferably uses the roller diameter more than 1 to be the working roll below the 700mm.Thus, can promote near the formation of the texture that the top layer is, therefore compare, Young's modulus is improved with obsolete occasion.From this viewpoint, with work roll diameter be defined as below the 700mm, be preferably below the 600mm, more preferably below the 500mm.The lower limit of work roll diameter does not have special stipulation, but for 300mm when following logical plate control become difficult.Use the upper limit of the passage of minor diameter roller not have special stipulation, such as described above, the hot finishing passage is generally about 8 passages.
With the hot-rolled steel sheet of making like this, it is preferred being up to the thermal treatment that Da Wendu is 500～950 ℃ a scope (annealing) after pickling.Thus, the Young's modulus of rolling direction further improves.Although this reason determines as yet, by inference, be since the dislocation that the phase transformation after rolling is introduced through due to Overheating Treatment arranges once more.
When being up to Da Wendu and being lower than 500 ℃, its effect is not remarkable, on the other hand, α → γ phase transformation takes place when surpassing 950 ℃, so its result, and the gathering of texture is identical or die down, and Young's modulus also is the tendency of deterioration.Therefore, be defined as the lower limit and the upper limit respectively with 500 ℃ and 950 ℃.
This scope that is up to Da Wendu is preferably 650 ℃～850 ℃.
This heat treating method is not particularly limited, and gets final product at common continuous annealing line and pack annealing and continuous hot-dipping zinc wire described later etc.
Also can be to implementing cold rolling and thermal treatment (annealing) after the hot-rolled steel sheet pickling.Cold rolling rate is for being lower than 60%.This is because if cold rolling rate is more than 60%, and then great changes have taken place in the texture meeting of the raising Young's modulus of hot-rolled steel sheet formation, and the Young's modulus of rolling direction reduces.
Thermal treatment is implemented in cold rolling end back.This heat treated Da Wendu of being up to is 500～950 ℃ a scope.Young's modulus raising degree reduces when being lower than 500 ℃, and some occasion processibility deterioration, therefore is defined as lower limit with 500 ℃.On the other hand, when thermal treatment temp surpasses 950 ℃, α → γ phase transformation takes place, therefore consequently, the gathering of texture is identical or die down, and Young's modulus also is the tendency of deterioration.Therefore, be defined as the lower limit and the upper limit respectively with 500 ℃ and 950 ℃.
This preferable range that is up to Da Wendu is 600 ℃～850 ℃.
The rate of heating that arrives maximum heating temperature is not particularly limited, and preferably is defined as 3～70 ℃/second scope.When rate of heating is lower than 3 ℃/second, add and pine for carrying out recrystallize, defeated and dispersed to the texture that Young's modulus is favourable.Material behavior does not change especially when surpassing 70 ℃/second, therefore preferably this value is defined as the upper limit.
After the above-mentioned thermal treatment, carry out once up to 550 ℃, be preferably up to the cooling below 450 ℃, it also is possible implementing thermal treatments in 150～550 ℃ again.These various purposes such as organizational controls according to the promotion of the phase transformation of the control of solid solution C amount and martensitic tempering, bainite etc. select suitable condition to get final product.
The tissue of the steel plate that obtains according to the manufacture method of the high young's modulus steel plate of the present embodiment, with ferrite or bainite as principal phase, two-phase mix to exist also can, having martensite, austenite, carbide, nitride in the tissue is that main compound is also passable.That is, characteristic is made tissue respectively and is got final product as requested.
(the 3rd embodiment)
In the 3rd embodiment, an example that the 1st, the 2nd above-mentioned embodiment is had hot-dip galvanized steel sheet, alloyed hot-dip galvanized steel plate, high Young's modulus steel pipe and their manufacture method of high Young's modulus describes.
Hot-dip galvanized steel sheet has the high young's modulus steel plate of the 1st, the 2nd embodiment and the galvanizing that this high young's modulus steel plate is implemented.Hot-rolled steel sheet or the cold rolling cold-rolled steel sheet that obtain of this hot-dip galvanized steel sheet after by means of the annealing that the 1st, the 2nd above-mentioned embodiment is obtained implemented galvanizing and made.
The composition of zinc coating is not particularly limited, and except zinc, it is also passable to add Fe, Al, Mn, Cr, Mg, Pb, Sn, Ni etc. as required.
Heat-treat with zinc-plated also passable at the continuous hot-dipping zinc wire cold rolling back.
Alloyed hot-dip galvanized steel plate have the 1st, the 2nd embodiment high young's modulus steel plate and to this high young's modulus steel plate implement alloyed hot-dip zinc-coated.This alloyed hot-dip galvanized steel plate is by means of above-mentioned hot-dip galvanized steel sheet being carried out Alloying Treatment and being made.
This Alloying Treatment is undertaken by implementing thermal treatment 450～600 ℃ scope.When being lower than 450 ℃, alloying can not fully be carried out, and alloying is carried out the coating embrittlement excessively when surpassing 600 ℃.Therefore, because the problem that the processing of punching press etc. causes that coating is peeled off etc.The time of Alloying Treatment was defined as more than 10 seconds.When being lower than 10 seconds, alloying can not be carried out fully.In the occasion of alloying hot-dip galvanized steel sheet, carry out pickling after the hot rolling as required, implementing draft in online or off-line then is that skin pass rolling below 10% is also passable.
The high Young's modulus steel pipe is the steel plate with high Young's modulus of the 1st, the 2nd embodiment, the steel pipe of reeling and to form to any direction for above-mentioned high young's modulus steel plate.For example, this high Young's modulus steel pipe is reeled in interior mode and to be made by the high young's modulus steel plate of above-mentioned the 1st, the 2nd embodiment is 0～30 ° with the angle between the length direction of rolling direction and steel pipe.Thus, can make the high high Young's modulus steel pipe of Young's modulus of the length direction of steel pipe.
Because reel abreast with rolling direction, it is the highest that Young's modulus becomes, and therefore preferred this angle is smaller as far as possible.From this viewpoint, more preferably reel with the angle below 15 °.As long as satisfy the relation of the length direction of rolling direction and steel pipe, pipe-making method can adopt any methods such as UO welded tube, butt seam welding pipe, helical welded tube.Certainly, will the high direction of Young's modulus not be defined as the direction that parallels with the steel pipe length direction,, make the high steel pipe of Young's modulus in any direction, without any problem according to purposes yet.
To above-mentioned high Young's modulus steel pipe, implementing Al is that coating and various plating are also passable.To hot-dip galvanized steel sheet, alloyed hot-dip galvanized steel plate and high Young's modulus steel pipe, can carry out the surface treatment of organic epithelium, inorganic epithelium and various coating etc. according to purpose.
Embodiment
Secondly, according to embodiment the present invention is described.
The embodiment of relevant the 1st, the 3rd embodiment is expressed as follows.
(embodiment 1)
Melting has the steel of the composition shown in table 1, the table 2, and implements hot rolling with the condition shown in table 3 and the table 4.The Heating temperature of this moment all is 1250 ℃.In altogether by 7 sections finishing stands that constitute, be defined as 0.21～0.24 scope at final 3 sections frictional coefficient with roll and steel plate, final 3 sections total draft is 70%.The skin-pass draft is 0.3%.
The mensuration of Young's modulus is to be measured by above-mentioned lateral resonance method.Take the JIS5 tensile test specimen, estimate the tensile properties of TD direction.And, the texture that the mensuration thickness of slab is 1/8 layer.
The results are shown in table 3 and table 4, therefrom know, with suitable condition the steel with chemical ingredients of the present invention is being carried out the hot rolled occasion, the Young's modulus of rolling direction can surpass 230GPPa.
At this, in the table of embodiment, FT represents that the final finish rolling outlet side of hot rolled temperature, CT represent that coiling temperature, TS represent that tensile strength, YS represent that yield strength, E1 represent Young's modulus, E (D) expression and the Young's modulus of RD direction direction at 45, the Young's modulus of E (TD) expression TD direction of unit elongation, E (RD) expression RD direction.These are identified in the later explanation is general.
Table 1
| Steel No. | C | Si | Mn | P | S | Al | N |
| A | 0.0040 | 0.01 | 3.01 | 0.010 | 0.0019 | 0.031 | 0.0024 |
| B | 0.0044 | 0.01 | 2.44 | 0.011 | 0.0022 | 0.028 | 0.0026 |
| C | 0.0036 | 0.01 | 1.95 | 0.008 | 0.0019 | 0.033 | 0.0031 |
| D | 0.0047 | 0.01 | 4.34 | 0.007 | 0.0025 | 0.029 | 0.0029 |
| E | 0.050 | 0.02 | 3.26 | 0.005 | 0.0034 | 0.022 | 0.0033 |
| F | 0.051 | 0.02 | 3.33 | 0.005 | 0.0037 | 0.027 | 0.0032 |
| G | 0.050 | 0.01 | 2.27 | 0.006 | 0.0034 | 0.030 | 0.0030 |
| H | 0.055 | 0.55 | 3.58 | 0.007 | 0.0016 | 0.024 | 0.0025 |
| I | 0.103 | 0.09 | 3.04 | 0.011 | 0.0020 | 0.035 | 0.0027 |
| J | 0.112 | 0.84 | 3.00 | 0.010 | 0.0020 | 1.660 | 0.0034 |
| K | 0.100 | 0.08 | 3.04 | 0.009 | 0.0018 | 0.032 | 0.0028 |
| L | 0.010 | 0.22 | 3.63 | 0.005 | 0.0027 | 0.037 | 0.0026 |
| M | 0.009 | 0.04 | 3.50 | 0.009 | 0.0031 | 0.031 | 0.0034 |
| N | 0.011 | 0.01 | 0.52 | 0.022 | 0.0053 | 0.033 | 0.0019 |
Table 2
| Steel No. | Mo | B | Ti | Nb | Other | Ar 3(℃) | Remarks |
| A | 0.28 | 0.0025 | - | - | - | 630 | Steel of the present invention |
| B | 0.25 | 0.0016 | 0.011 | 0.008 | - | 690 | Comparative steel |
| C | 0.17 | 0.0033 | 0.022 | - | - | 712 | Comparative steel |
| D | 0.29 | 0.0022 | 0.009 | 0.013 | - | 526 | Steel of the present invention |
| E | 0.52 | 0.0020 | 0.030 | 0.040 | - | 582 | Steel of the present invention |
| F | - | - | 0.029 | 0.038 | - | 649 | Comparative steel |
| G | 0.53 | 0.0024 | 0.025 | 0.041 | - | 656 | Comparative steel |
| H | 0.36 | 0.0037 | 0.014 | 0.022 | Cr＝0.40 | 560 | Steel of the present invention |
| I | 0.40 | 0.0019 | 0.018 | 0.019 | - | 599 | Steel of the present invention |
| J | 0.39 | 0.0020 | 0.020 | 0.019 | - | 949 | Comparative steel |
| K | 0.41 | - | 0.021 | 0.044 | V＝0.010 | 627 | Comparative steel |
| L | 0.33 | 0.0041 | - | 0.028 | - | 558 | Steel of the present invention |
| M | 0.42 | 0.0030 | - | - | Cu＝0.42 | 571 | Steel of the present invention |
| N | - | - | - | - | - | 887 | Comparative steel |
Table 3
Table 4
(embodiment 2)
For steel E and L in the hot-rolled steel sheet of embodiment 1, (being up to Da Wendu is 750 ℃ to implement continuous annealing (keeping 90 seconds at 700 ℃), pack annealing (keeping 6 hours at 700 ℃) and continuous hot-dipping galvanizing, the dipping back is 500 ℃ of Alloying Treatment of implementing for 20 seconds in the zinc plating bath), measure tensile properties and Young's modulus.
The results are shown in table 5.From table, clearly show, by with suitable condition the steel with chemical ingredients of the present invention being carried out hot rolling and carries out proper heat treatment, the Young's modulus raising.
(embodiment 3)
For steel E and L in the hot-rolled steel sheet of embodiment 1, after 30% draft is cold rolling, implement continuous hot-dipping galvanizing (make be up to Da Wendu do various variations, in the zinc plating bath dipping back in 500 ℃ of Alloying Treatment of implementing for 20 seconds), measure tensile properties and Young's modulus.
The results are shown in table 6.From table, clearly show,,, can obtain the good cold-rolled steel sheet of Young's modulus of RD direction and TD direction again by suitable thermal treatment by the steel with chemical ingredients of the present invention being carried out hot rolling and cold rolling with suitable condition.But, being up to significantly high occasion of Da Wendu, Young's modulus also slightly reduces.
(embodiment 4)
For steel E and L in the hot-rolled steel sheet of embodiment 1, carry out following processing.
At the continuous hot-dipping zinc wire steel plate is heated to 650 ℃, is cooled to impregnated in after about 470 ℃ during 460 ℃ fused zinc bathes.The thickness of coating of zinc is in weight per unit area single face average out to 40g/m
2After galvanizing, resemble and surface of steel plate is implemented (1) organic lining and (2) application following, measure tensile properties and Young's modulus.
The results are shown in table 7.From table, know and know, implement the steel plate of galvanizing, give organic epithelium and coating to the surface again, have good Young's modulus.
(1) organic epithelium
At the resin solid composition is that 27.6 quality %, dispersion liquid viscosity are that 1400mPas (25 ℃), pH are 8.8, the ammonia salt (COONH of carboxyl
4) content be that the content of 9.5 quality %, the carboxyl of whole resin solid composition is that 2.5 quality %, the dispersible granule mean diameter of whole resin solid composition is in the water-base resin of about 0.030 μ m, add the corrosion inhibitor of 4 quality %, 12% colloid silica, make antirust treatment solution.Should be coated on above-mentioned steel plate by roller coating machine by antirust treatment solution, arriving temperature according to the surface of steel plate is that 120 ℃ mode is carried out drying, makes it form the thick epithelium of about 1 μ m.
(2) application
Through on the above-mentioned steel plate of degreasing, apply Japanese パ-カ ラ イ ジ Application グ corporate system " ZM1300AN " by roller coating machine as the chemical conversion processing.Then, be that 60 ℃ condition makes it carry out warm air drying to arrive temperature.The adhesion amount that chemical conversion is handled is counted 50mg/m with the adhesion amount of Cr
2Again the steel plate of implementing the chemical conversion processing is applied priming paint, another side is applied CB coating one side respectively with roller coating machine.Adopt then and make its dry sclerosis with the induction type process furnace of hot blast.The arrival temperature of this moment is 210 ℃.
On the face that has applied priming paint,, adopt then and be 230 ℃ and make its dry sclerosis to arrive temperature with the induction type process furnace of hot blast with roller curtain formula curtain coater coating finish paint.In addition, priming paint uses Japanese Off ァ イ Application コ-テ Application グ ス corporate system " FL640EU priming paint ", is coated with in dry film thickness and dresses up 5 μ m.CB coating uses Japanese Off ァ イ Application コ-テ Application グ ス corporate system " FL100HQ ", is coated with in dry film thickness and dresses up 5 μ m.Finish paint uses Japanese Off ァ イ Application コ-テ Application グ ス corporate system " FL100HQ ", is coated with in dry film thickness and dresses up 15 μ m.
(embodiment 5)
Use steel E and the L shown in the table 1, it is rolling to carry out different circumferential speed.At final 3 sections circumferential speed is changed in altogether by 7 sections finishing stands that constitute, the measurement result of hot-rolled condition and tensile properties and Young's modulus is shown in table 8.The hot-rolled condition of not expressing in table 8 is all identical with embodiment 1.
Clearly show that from table when with suitable condition the steel with chemical ingredients of the present invention being carried out hot rolling, if rolling with 1 different circumferential speed of implementing more than 1% more than the passage, can promote near the formation of the texture that the top layer is, Young's modulus further improves.
(embodiment 6)
Use steel E and the L shown in the table 1, carry out thin footpath rolling system.At final 3 sections roller diameter is changed in altogether by 7 sections finishing stands that constitute, the measurement result of hot-rolled condition and tensile properties and Young's modulus is shown in table 9.The hot-rolled condition of not expressing in table 9 is all identical with embodiment 1.
From table, clearly show, when the steel with chemical ingredients of the present invention being carried out hot rolling with suitable condition, if use roller footpath to implement 1 rolling more than the passage as the roll below the 700mm, can promote near the formation of the texture the top layer, Young's modulus further improves.
(embodiment 7)
Secondly, the embodiment with the 2nd, the 3rd embodiment is expressed as follows.
Melting has the steel of the composition shown in table 10～13, implements hot rolling with the condition shown in table 14～19.The Heating temperature of this moment all is defined as 1230 ℃.In altogether by 7 sections finishing stands that constitute, be defined as 0.21～0.24 scope at final 3 sections frictional coefficient with roll and steel plate, final 3 sections total draft is 55%.The skin-pass draft all is 0.3%.
The mensuration of Young's modulus is to be measured by above-mentioned lateral resonance method.Take the JIS5 tensile test specimen, estimate the tensile properties of TD direction.And, the texture that 1/8 layer of thickness of slab of mensuration and thickness of slab are 7/16 layer.
The results are shown in table 14～19.In addition, table 15 is that continuous table, the table 17 of table 14 are that continuous table, the table 19 of table 16 is continuous tables of table 18.Table and should the continuous table of table in, with the value representation of delegation record numerical value about same sample.This also is a common in specification sheets and in the later table.The value representation extraneous value of the present invention that has underscore in the table.This is identified in the explanation of later table also is common.
Clearly show that from table 14～19 with suitable condition the steel with chemical ingredients of the present invention is being carried out the hot rolled occasion, the Young's modulus of rolling direction can surpass 230GPPa.
(embodiment 8)
Melting has the plate slab of the composition of table 10,11 steel No.C and L, implements hot rolling with the condition shown in the table 20.The Heating temperature of slab all is defined as 1230 ℃.About other rolling condition, in altogether by 7 sections finishing stands that constitute, be defined as 0.21～0.24 scope at final 3 sections frictional coefficient with roll and steel plate, final 3 sections total draft is 55%.The skin-pass draft all is 0.3%.In addition, Ar
3Identical with the occasion of table 14 and 16.
Continuous annealing (keeping 90 seconds at 700 ℃), pack annealing (keeping 6 hours at 700 ℃) and continuous hot-dipping galvanizing are implemented in rolling back, and (being up to Da Wendu is 750 ℃, dipping back is 500 ℃ of Alloying Treatment of implementing for 20 seconds in the zinc plating bath) any processing, measure tensile properties and Young's modulus.
The results are shown in table 20 and 21.In addition, table 21 is continuous tables of table 20.From table, clearly show, by with suitable condition the steel with chemical ingredients of the present invention being carried out hot rolling and carries out suitable thermal treatment, the Young's modulus raising.
(embodiment 9)
Melting has the plate slab of the composition of table 10,11 steel No.C and L, implements hot rolling with the condition shown in the table 22.The Heating temperature of slab all is defined as 1230 ℃.About other rolling condition, in altogether by 7 sections finishing stands that constitute, be defined as 0.21～0.24 scope at final 3 sections frictional coefficient with roll and steel plate, final 3 sections total draft is 55%.The skin-pass draft all is 0.3%.In addition, Ar
3Identical with the occasion of table 14 and 16.
Carry out cold rollingly after the hot rolling, implement continuous hot-dipping galvanizing (make to be up to Da Wendu and to carry out various variations, the dipping back is in 500 ℃ of Alloying Treatment of implementing for 20 seconds in the zinc plating bath) again.Measure tensile properties and Young's modulus then.
The results are shown in table 22 and 23.In addition, table 23 is continuous tables of table 22.From table, clearly show,, may obtain the good cold-rolled steel sheet of Young's modulus of RD direction and TD direction by the steel with chemical ingredients of the present invention being carried out hot rolling and cold rolling and carry out proper heat treatment with suitable condition.But, being up to significantly high occasion of Da Wendu, Young's modulus also slightly reduces.
(embodiment 10)
Melting has the plate slab of the composition of table 10,11 steel No.C and L, implements hot rolling with the condition shown in the table 24.The Heating temperature of slab all is defined as 1230 ℃.About other rolling condition, in altogether by 7 sections finishing stands that constitute, be defined as 0.21～0.24 scope at final 3 sections frictional coefficient with roll and steel plate, final 3 sections total draft is 55%.The skin-pass draft all is 0.3%.In addition, Ar
3Identical with the occasion of table 14 and 16.
After the hot rolling, steel plate is heated to 650 ℃, is cooled to impregnated in after about 470 ℃ in 460 ℃ the fused zinc plating bath at the continuous hot-dipping zinc wire.The thickness of coating of zinc is in weight per unit area single face average out to 40g/m
2After galvanizing, resemble and surface of steel plate is implemented (1) organic lining and (2) application following, measure tensile properties and Young's modulus.
(1) organic epithelium
At the resin solid composition is that 27.6 quality %, dispersion liquid viscosity are that 1400mPas (25 ℃), pH are 8.8, the ammonia salt (COONH of carboxyl
4) content be that the content of 9.5 quality %, the carboxyl of whole resin solid composition is that 2.5 quality %, the dispersible granule mean diameter of whole resin solid composition is in the water-base resin of about 0.030 μ m, add the corrosion inhibitor of 4 quality %, 12% colloid silica, make antirust treatment solution.Should be coated on above-mentioned steel plate by roller coating machine by antirust treatment solution, arriving temperature according to the surface of steel plate is that 120 ℃ mode is carried out drying, makes it form the thick epithelium of about 1 μ m.
(2) application
Through on the above-mentioned steel plate of degreasing, apply Japanese パ-カ ラ イ ジ Application グ corporate system " ZM1300AN " as the chemical conversion processing by roller coating machine, make it carry out warm air drying with the condition that arrives 60 ℃ of temperature.The adhesion amount that chemical conversion is handled is counted 50mg/m with the adhesion amount of Cr
2Again to implemented steel plate that chemical conversion handles with roller coating machine respectively to steel plate simultaneously apply priming paint, to another side coating CB coating, adopt and make its dry sclerosis with the induction type process furnace of hot blast.The arrival temperature of this moment is 210 ℃.
Again in application on the face of priming paint, with roller curtain formula curtain coater coating finish, adopt then and be 230 ℃ and make its dry sclerosis to arrive temperature with the induction type process furnace of hot blast.Priming paint uses Japanese Off ァ イ Application コ-テ Application グ ス corporate system " FL640EU priming paint ", is coated with in dry film thickness and dresses up 5 μ m.CB coating uses Japanese Off ァ イ Application コ-テ Application グ ス corporate system " FL100HQ ", is coated with in dry film thickness and dresses up 5 μ m.Finish paint uses Japanese Off ァ イ Application コ-テ Application グ ス corporate system " FL100HQ ", is coated with in dry film thickness and dresses up 15 μ m.
The results are shown in table 24 and 25.In addition, table 25 is continuous tables of table 24.Clearly from table know that the steel plate of implementing the steel plate of galvanizing and having revested organic epithelium and coating on the surface also has good Young's modulus.
(embodiment 11)
Melting has table 10,11 steel No.C and L steel, and it is rolling to carry out different circumferential speed.In altogether by 7 sections finishing stands that constitute, circumferential speed is changed at final 3 sections.The measurement result of hot-rolled condition and tensile properties and Young's modulus is shown in table 26.The hot-rolled condition of not expressing at table 26 is fully identical with embodiment 7.
Resulting table 26 and 27 of the results are shown in.In addition, table 27 is continuous tables of table 26.Clearly show that from table when the steel with chemical ingredients of the present invention is carried out hot rolling with suitable condition, if it is rolling to implement the above different circumferential speed more than 1% of 1 passage, can promote that near the texture the top layer forms, Young's modulus further improves.
(embodiment 12)
Adopt table 10,11 steel No.C and L steel, carry out thin footpath rolling system.In altogether by 7 sections finishing stands that constitute, roller diameter is changed at final 3 sections.The measurement result of hot-rolled condition and tensile properties and Young's modulus is shown in table 28.The hot-rolled condition of not expressing at table 28 is fully identical with embodiment 7.
Resulting table 28 and 29 of the results are shown in.In addition, table 29 is continuous tables of table 28.Thus, when the steel with chemical ingredients of the present invention is carried out hot rolling with suitable condition, if use the above roller footpath of 1 passage to be the roll below the 700mm, can promote that near the texture the top layer forms, Young's modulus further improves.
(embodiment 13)
Steel shown in table 30～33 are heated to 1200～1270 ℃, carry out hot rolling, make the thick hot-rolled steel sheet of 2mm with the hot-rolled condition shown in the table 34,36,38,40.At this, for having carried out the annealed hot-rolled steel sheet, in hot-rolled sheet annealing (3
*) be designated as " having " in the hurdle, to not carried out the annealed hot-rolled steel sheet, be designated as " nothing ".This annealing is carried out with 600～700 ℃, 60 minutes condition.This is identified in the explanation of later table general.
The mensuration of the Young's modulus on top layer is to be that the thickness of thickness of slab 1/6 cuts sample with the distance top layer, and measures with above-mentioned resonant method.About tensile properties, take the JIS5 tensile test specimen to estimate at width.
The evaluation of shape freezing use 260mm length * 50mm wide * the rectangular sample of thickness of slab, adopt the wide 78mm of being of drift, drift shoulder to be configured as hat for R4mm and with the wrinkle resistant thickness of compressive plate of various differences, tie up the shape of the wide central section of shape measuring apparatus assay plate with 3 then for R5mm, punch die shoulder.As shown in Figure 1, the angle that intersects from the line of the line of an A and some B and some C and some D deduct 90 ° difference about mean value as springback capacity, some C and the inverse of putting the radius-of-curvature ρ [mm] between the E after left and right sides equalization on duty is with 1000 times as the wall amount of warpage, thereby the evaluation shape freezing.1000/ ρ is more little, and then shape freezing is good more.In addition, carry out bending in the mode of vertically introducing broken line with rolling direction.
Usually know, when armor plate strength raises, the shape freezing deterioration.The present inventor is from carrying out the result that actual parts are shaped, the blank holder pressure of measuring according to aforesaid method is springback capacity and 1000/ ρ of 70N, is respectively (0.015 * TS-6 (°) following and (0.01 * TS-36 (mm for the tensile strength [MPa] of steel plate
-1) following occasion because the property freezed of this moment is good, therefore with satisfy simultaneously this two as good shape freezing condition, estimate.
Resulting table 34～41 that the results are shown in.In addition, table 35 is that continuous table, the table 37 of table 34 are that continuous table, the table 39 of table 36 is that continuous table, the table 41 of table 38 is continuous tables of table 40.Wherein, in the table for draft (1
*), the occasion more than 50% of adding up at the hot rolled draft is designated as " suitable "; Occasion being lower than 50% is designated as " improper ".For frictional coefficient (2
*), the average friction coefficient in hot rolling is designated as " suitable " above 0.2 occasion; Occasion below 0.2 is designated as " improper ".Shape freezing is designated as " well " in the occasion that satisfies above-mentioned 2 conditions, is designated as " bad " in ungratified occasion.These are marked in the explanation of later table general.When blank holder pressure increased, 1000/ ρ had the tendency that reduces.But, no matter select which type of blank holder pressure, the grade of the quality of the shape freezing of steel plate does not change.Therefore blank holder pressure is the shape freezing that the evaluation of 70kN can be represented steel plate well.
(embodiment 14)
Use steel P5 and the P8 shown in the table 30,31, it is rolling to carry out different circumferential speed.In the finishing mill frame that constitutes by 6 sections altogether, circumferential speed is changed at final 3 sections.The measurement result of hot-rolled condition, tensile properties, Young's modulus and the evaluation result of shape freezing are shown in table 42.Creating conditions of not describing in the table is identical with embodiment 13.
The results are shown in table 42 and 43 with what obtain.In addition, table 43 is continuous tables of table 42.Clearly show in the table that when with suitable condition the steel with chemical ingredients of the present invention being carried out hot rolling, if it is rolling to implement the above different circumferential speed more than 1% of 1 passage, then near the Young's modulus the top layer further improves, shape freezing is good.
(embodiment 15)
Use steel P5 and the P8 shown in the table 30,31, carry out thin footpath rolling system.In the finishing mill frame that constitutes by 6 sections altogether, roller diameter is changed at final 3 sections.The measurement result of hot-rolled condition, tensile properties, Young's modulus and the evaluation result of shape freezing are shown in table 44.Creating conditions of not describing in the table is identical with embodiment 13.
The results are shown in table 44 and 45 with what obtain.In addition, table 45 is continuous tables of table 44.Clearly show in the table that when with suitable condition the steel with chemical ingredients of the present invention being carried out hot rolling, if use the following roll of the above 700mm of 1 passage, then near the Young's modulus the top layer further improves the shape freezing raising.
(embodiment 16)
Use steel P5 and the P8 shown in the table 30,31, make cold rolled annealed steel plate.Hot rolling, cold rolling, annealing conditions, tensile properties, the measurement result of Young's modulus and the evaluation result of shape freezing are shown in table 46.Creating conditions of not describing in the table is identical with embodiment 13.
The results are shown in table 46 and 47 with what obtain.In addition, table 47 is continuous tables of table 46.Clearly show in the table that if when with suitable condition the steel with chemical ingredients of the present invention being carried out hot rolling, cold rolling and annealing, then the Young's modulus on top layer surpasses 245GPa, shape freezing raising.
High young's modulus steel plate of the present invention can be used for automobile, household appliances goods and buildings etc.High young's modulus steel plate of the present invention comprises the hot-rolled steel sheet of surface treated narrow sense not and cold-rolled steel sheet, for antirust and implemented surface-treated generalized hot-rolled steel sheet and cold-rolled steel sheets such as galvanizing, alloyed hot-dip zinc-coated and plating.And, also comprise the steel plate of the coating of aluminium system.The surface that also comprises these hot-rolled steel sheets, cold-rolled steel sheet and various Coated Steels has the steel plate of organic epithelium, inorganic epithelium, coating etc. and the steel plate that the surface has their multiple combination.
High young's modulus steel plate of the present invention is the steel plate with high Young's modulus, therefore in use, may reduce the possibility of result lightweight than the thickness of former steel plate.Therefore, ball is possessed profit over the ground.
Adopt high young's modulus steel plate of the present invention can improve shape freezing, high tensile steel plate becomes easy to automobile with the suitable of punch components such as member.In addition, the striking energy absorption characteristic of steel plate of the present invention is also good, therefore helps the raising of the security of automobile.
Claims (46)
1. high young's modulus steel plate, it is characterized in that, in quality % contain C:0.0005～0.30%, below the Si:2.5%, Mn:2.7～5.0%, below the P:0.15%, below the S:0.015%, Mo:0.15～1.5%, B:0.0006～0.01%, below the Al:0.15%, and surplus is made of Fe and unavoidable impurities, 1/8 layer of thickness of slab 110}＜223〉with 110}＜111〉the utmost point density of either party or the two be more than 10, the Young's modulus of rolling direction surpasses 230GPa.
2. high young's modulus steel plate according to claim 1 is characterized in that, 1/2 layer of thickness of slab 112}＜110〉and utmost point density be more than 6.
3. high young's modulus steel plate according to claim 1 is characterized in that, also contains a kind or 2 kinds among Ti:0.001～0.20 quality %, Nb:0.001～0.20 quality %.
4. high young's modulus steel plate according to claim 1, it is characterized in that deducting the BH amount that the difference of the flow stress that stretched estimates at 2% o'clock by the upper yield point of 2% back when implementing thermal treatments in 20 minutes and carrying out tension test once again for 170 ℃ that stretch is 5MPa～200MPa.
5. high young's modulus steel plate according to claim 1 is characterized in that, also contains Ca:0.0005～0.01 quality %.
6. high young's modulus steel plate according to claim 1 is characterized in that, also contain among Sn, Co, Zn, W, Zr, V, Mg, the REM more than a kind or 2 kinds, their total content is 0.001～1.0 quality %.
7. high young's modulus steel plate according to claim 1 is characterized in that, also contain among Ni, Cu, the Cr more than a kind or 2 kinds, their total content is 0.001～4.0 quality %.
8. a hot-dip galvanized steel sheet is characterized in that, the galvanizing that has the described high young's modulus steel plate of claim 1 and apply on described high young's modulus steel plate.
9. an alloyed hot-dip galvanized steel plate is characterized in that, have the described high young's modulus steel plate of claim 1 and on described high young's modulus steel plate, apply alloyed hot-dip zinc-coated.
10. a high Young's modulus steel pipe is characterized in that, have the described high young's modulus steel plate of claim 1, and described high young's modulus steel plate is reeled to any direction.
11. the manufacture method of high young's modulus steel plate according to claim 1, it is characterized in that, have slab is heated to temperature more than 950 ℃ is made hot-rolled steel sheet to implement hot rolling operation, described slab in quality % contain C:0.0005～0.30%, below the Si:2.5%, Mn:2.7～5.0%, below the P:0.15%, below the S:0.015%, Mo:0.15～1.5%, B:0.0006～0.01%, below the Al:0.15%, and surplus is made of Fe and unavoidable impurities; Wherein said hot-rolled process carries out under the following conditions: in surpassing 0.2 and to add up to draft be that mode more than 50% is rolled with the frictional coefficient of roll and steel plate below 800 ℃, and in Ar
3Finish hot rolling under the temperature of transformation temperature～750 ℃.
12. the manufacture method of high young's modulus steel plate according to claim 11 is characterized in that, in described hot-rolled process, the different circumferential speed of implementing 1 passage at least is that the different circumferential speed more than 1% is rolling.
13. the manufacture method of high young's modulus steel plate according to claim 11 is characterized in that, in described hot-rolled process, uses the roller footpath more than 1 to be the roll below the 700mm at least.
14. the manufacture method of high young's modulus steel plate according to claim 11, it is characterized in that the hot-rolled steel sheet that also has after described hot rolling finished is that 500 ℃～950 ℃ condition is carried out the annealed operation with continuous annealing line or pack annealing to be up to Da Wendu.
15. the manufacture method of high young's modulus steel plate according to claim 11, it is characterized in that, comprise that also the hot-rolled steel sheet after described hot rolling finished implements cold rolling operation to be lower than 60% draft, and after described cold rolling process, carry out the annealed operation.
16. the manufacture method of high young's modulus steel plate according to claim 11 is characterized in that, also has: described hot-rolled steel sheet is implemented cold rolling operation to be lower than 60% draft; Behind described cold rolling process, be that 500 ℃～950 ℃ condition is carried out the annealed operation to be up to Da Wendu; And below described annealing operation postcooling to 550 ℃, then in 150～550 ℃ of operations of heat-treating.
17. the manufacture method of a hot-dip galvanized steel sheet is characterized in that, has: the operation of the high young's modulus steel plate of having annealed by the manufacture method manufacturing of the described high young's modulus steel plate of claim 14; And the operation of described high young's modulus steel plate being implemented galvanizing.
18. the manufacture method of an alloyed hot-dip galvanized steel plate is characterized in that, has: the operation of making hot-dip galvanized steel sheet by the manufacture method of the described hot-dip galvanized steel sheet of claim 17; And described hot-dip galvanized steel sheet carried out heat treated operation more than 10 seconds 450～600 ℃ temperature range.
19. the manufacture method of a hot-dip galvanized steel sheet is characterized in that, has: the operation of the high young's modulus steel plate of having annealed by the manufacture method manufacturing of the described high young's modulus steel plate of claim 15; And the operation of described high young's modulus steel plate being implemented galvanizing.
20. the manufacture method of an alloyed hot-dip galvanized steel plate is characterized in that, has: the operation of making hot-dip galvanized steel sheet by the manufacture method of the described hot-dip galvanized steel sheet of claim 19; And described hot-dip galvanized steel sheet carried out heat treated operation more than 10 seconds 450～600 ℃ temperature range.
21. the manufacture method of a high Young's modulus steel pipe is characterized in that, has: the operation of making high young's modulus steel plate by the manufacture method of the described high young's modulus steel plate of claim 11; With described high young's modulus steel plate is reeled and is made steel pipe to any direction.
22. a high young's modulus steel plate is characterized in that, in quality % contain C:0.0005～0.30%, below the Si:2.5%, Mn:0.1～5.0%, below the P:0.15%, below the S:0.015%, below the Al:0.15%, below the N:0.01%; And contain in mass percent～0.2%, B:0.0001～0.01% of Mo:0.005～1.5%, Nb:0.005～0.20%, Ti:48/14 * N more than a kind or 2 kinds, add up to 0.015～1.91 quality %; And surplus is made of Fe and unavoidable impurities; Wherein, 1/8 layer of thickness of slab 110}＜223〉and/or 110}＜111〉and utmost point density be more than 10, the Young's modulus of rolling direction surpasses 230GPa.
23. high young's modulus steel plate according to claim 22, it is characterized in that, contain whole described Mo, Nb, Ti, B, their content is respectively mass percent～0.2%, B:0.0006～0.01% of Mo:0.15～1.5%, Nb:0.01～0.20%, Ti:48/14 * N, and 1/8 layer of thickness of slab 110}＜001〉utmost point density be below 3.
24. high young's modulus steel plate according to claim 22 is characterized in that, 1/8 layer of described thickness of slab 110}＜001〉and utmost point density be below 6.
25. high young's modulus steel plate according to claim 22 is characterized in that, is being that the Young's modulus of 1/8 layer rolling direction is more than the 240GPa apart from the top layer of thickness of slab at least.
26. high young's modulus steel plate according to claim 22 is characterized in that, 1/2 layer of thickness of slab 211}＜011〉and utmost point density be more than 6.
27. high young's modulus steel plate according to claim 22 is characterized in that, 1/2 layer of thickness of slab 332}＜113〉and utmost point density be more than 6.
28. high young's modulus steel plate according to claim 22 is characterized in that, 1/2 layer of thickness of slab 100}＜011〉and utmost point density be below 6.
29. high young's modulus steel plate according to claim 22, it is characterized in that deducting the BH amount that the difference of the flow stress that stretched estimates at 2% o'clock by the upper yield point of 2% back when implementing thermal treatments in 20 minutes and carrying out tension test once again for 170 ℃ that stretch is 5MPa～200MPa.
30. high young's modulus steel plate according to claim 22 is characterized in that, also contains Ca:0.0005～0.01 quality %.
31. high young's modulus steel plate according to claim 22 is characterized in that, also contain among Sn, Co, Zn, W, Zr, V, Mg, the REM more than a kind or 2 kinds, their total content is 0.001～1.0 quality %.
32. high young's modulus steel plate according to claim 22 is characterized in that, also contain among Ni, Cu, the Cr more than a kind or 2 kinds, their total content is 0.001～4.0 quality %.
33. a hot-dip galvanized steel sheet is characterized in that, the galvanizing that has the described high young's modulus steel plate of claim 22 and apply on described high young's modulus steel plate.
34. an alloyed hot-dip galvanized steel plate is characterized in that, have the described high young's modulus steel plate of claim 22 and on described high young's modulus steel plate, apply alloyed hot-dip zinc-coated.
35. a high Young's modulus steel pipe is characterized in that, have the described high young's modulus steel plate of claim 22, and described high young's modulus steel plate is reeled to any direction.
36. the manufacture method of high young's modulus steel plate according to claim 22, it is characterized in that, have slab be heated to temperature more than 1000 ℃ is made hot-rolled steel sheet to implement hot rolling operation, described slab in quality % contain C:0.0005～0.30%, below the Si:2.5%, Mn:0.1～5.0%, below the P:0.15%, below the S:0.015%, below the Al:0.15%, below the N:0.01%; And contain in mass percent～0.2%, B:0.0001～0.01% of Mo:0.005～1.5%, Nb:0.005～0.20%, Ti:48/14 * N more than a kind or 2 kinds, add up to 0.015～1.91 quality %; And surplus is made of Fe and unavoidable impurities; Wherein said hot-rolled process carries out under the following conditions: the Effective strain amount ε that surpasses 0.2, calculated by following formula [1] with the frictional coefficient of roll and steel plate
*Be more than 0.4 and to add up to draft be that mode more than 50% is rolled, and in Ar
3Finish hot rolling under the temperature of transformation temperature～900 ℃,
N is finish rolling hot rolled rolling machine frame number, ε in the formula
jBe strain, the ε that the j frame applies
nBe strain, the t that the n frame applies
iBe the working time between i frame～i+1 frame, the rolling temperature T that τ i can pass through gas law constant R and i frame
iCalculated by following formula [2], the unit of wherein said working time is second, R=1.987, described rolling temperature T
iUnit be K,
T
i＝8.46×10
-9×exp{43800/R/T
i} [2]。
37. the manufacture method of high young's modulus steel plate according to claim 36 is characterized in that, in described hot-rolled process, the different circumferential speed that applies the above different circumferential speed of 1 passage at least and be more than 1% is rolling.
38. the manufacture method of high young's modulus steel plate according to claim 36 is characterized in that, in described hot-rolled process, uses the roller footpath more than 1 to be the roll below the 700mm at least.
39. the manufacture method of high young's modulus steel plate according to claim 36, it is characterized in that the hot-rolled steel sheet that also has after described hot rolling finished is that 500 ℃～950 ℃ condition is carried out the annealed operation with continuous annealing line or pack annealing to be up to Da Wendu.
40. the manufacture method of high young's modulus steel plate according to claim 36, it is characterized in that, comprise that also the hot-rolled steel sheet after described hot rolling finished implements cold rolling operation to be lower than 60% draft, and after described cold rolling process, carry out the annealed operation.
41. the manufacture method of high young's modulus steel plate according to claim 36 is characterized in that, also has: described hot-rolled steel sheet is implemented cold rolling operation to be lower than 60% draft; After described cold rolling process, be that 500 ℃～950 ℃ condition is carried out the annealed operation to be up to Da Wendu; And below described annealing operation postcooling to 550 ℃, then in 150～550 ℃ of operations of heat-treating.
42. the manufacture method of a hot-dip galvanized steel sheet, it is characterized in that, have: the operation of the high young's modulus steel plate of having annealed by the manufacture method manufacturing of the described high young's modulus steel plate of claim 39, and the operation of described high young's modulus steel plate being implemented galvanizing.
43. the manufacture method of an alloyed hot-dip galvanized steel plate, it is characterized in that, have: the manufacture method by the described hot-dip galvanized steel sheet of claim 42 is made the operation of hot-dip galvanized steel sheet, and to described hot-dip galvanized steel sheet 450～600 ℃ of heat treated operations of implementing more than 10 seconds.
44. the manufacture method of a hot-dip galvanized steel sheet, it is characterized in that, have: the operation of the high young's modulus steel plate of having annealed by the manufacture method manufacturing of the described high young's modulus steel plate of claim 40, and the operation of described high young's modulus steel plate being implemented galvanizing.
45. the manufacture method of an alloyed hot-dip galvanized steel plate, it is characterized in that, have: the manufacture method by the described hot-dip galvanized steel sheet of claim 44 is made the operation of hot-dip galvanized steel sheet, and to described hot-dip galvanized steel sheet 450～600 ℃ of heat treated operations of implementing more than 10 seconds.
46. the manufacture method of a high Young's modulus steel pipe, it is characterized in that, have: make the operation of high young's modulus steel plate and described high young's modulus steel plate is made steel pipe to any direction coiling by the manufacture method of the described high young's modulus steel plate of claim 36.
Applications Claiming Priority (5)
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|---|---|---|---|
| JP218132/2004 | 2004-07-27 | ||
| JP2004218132A JP4445339B2 (en) | 2004-01-08 | 2004-07-27 | High Young's modulus steel plate and manufacturing method thereof |
| JP330578/2004 | 2004-11-15 | ||
| JP019942/2005 | 2005-01-27 | ||
| JP207043/2005 | 2005-07-15 |
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Families Citing this family (17)
| Publication number | Priority date | Publication date | Assignee | Title |
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| JP5549414B2 (en) * | 2010-06-23 | 2014-07-16 | Ｊｆｅスチール株式会社 | Cold-rolled thin steel sheet having excellent shape freezing property and manufacturing method thereof |
| CA2831551C (en) | 2011-04-13 | 2016-03-08 | Nippon Steel & Sumitomo Metal Corporation | Hot-rolled steel sheet and method of producing the same |
| TWI457448B (en) | 2011-04-13 | 2014-10-21 | Nippon Steel & Sumitomo Metal Corp | High strength cold rolled steel sheet with excellent natural |
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| WO2012161241A1 (en) | 2011-05-25 | 2012-11-29 | 新日鐵住金株式会社 | Cold-rolled steel sheet and method for producing same |
| CN102373324B (en) * | 2011-11-11 | 2012-12-19 | 江苏华程工业制管股份有限公司 | Heat treatment process of hot-rolled steel tube |
| BR112014017109B1 (en) | 2012-01-13 | 2019-04-02 | Nippon Steel & Sumitomo Metal Corporation | HOT LAMINATED STEEL SHEET AND MANUFACTURING PROCESS |
| JP5982905B2 (en) * | 2012-03-19 | 2016-08-31 | Ｊｆｅスチール株式会社 | Method for producing high-strength hot-dip galvanized steel sheet |
| JP5982906B2 (en) * | 2012-03-19 | 2016-08-31 | Ｊｆｅスチール株式会社 | Method for producing high-strength hot-dip galvanized steel sheet |
| CN103667917A (en) * | 2013-11-08 | 2014-03-26 | 铜陵安东铸钢有限责任公司 | High-temperature-resistant low-carbon steel material and preparation method thereof |
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| CN115109994B (en) * | 2021-03-22 | 2023-09-12 | 宝山钢铁股份有限公司 | High-strength cold-rolled hot-dip galvanized microalloy strip steel and manufacturing method thereof |
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2005
- 2005-07-27 CN CNB2005800251600A patent/CN100526493C/en not_active Expired - Fee Related
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