high strength steel sheet and high strength galvanized steel sheet excellent in conformability and p

专利摘要:
patent specification report for "high strength steel sheet and high strength galvanized steel sheet excellent in conformability and production methods". Field of the art The present invention relates to a high strength steel sheet and a high strength galvanized steel sheet which are excellent in conformability and production methods thereof. background to the technique in recent years, there has been an increase in demands for greater strength in the steel plate that is used for automobiles etc. in particular, for the purpose of increasing crash safety, etc., a high strength steel plate with a maximum tensile strength of 900 mpa or more is also used. This high strength steel sheet is economically formed in large volumes by press work in the same way as mild steel sheet and is used as structural elements. however, recently, together with the rapid increase in strength of high strength steel plate, particularly high strength steel plate with a maximum tensile strength of 900 mpa or more, a problem has arisen that conformability has become insufficient. and work accompanied by local deformation as stretch formability that becomes difficult. furthermore, when a high velocity tensile force acts on a steel material, there is the problem that the fracture mode could easily change from ductile fracture to embrittlement fracture. In the past, as an example of the technique of hardening a steel material, a high strength steel material that has been hardened upon satisfactory satisfactory precipitation of cu has been known. plt 1 describes a high strength precipitation hardened steel material of cu which contains c, si, p, s, al, n, and cu in predetermined ranges, contains one or both of mn: 0.1 to 3, 0% and cr: 0.1 to 3.0%, has a (mn + cr) / cu of 0.2 or more, and has an unavoidable iron balance and impurities, has an average crystal grain size of 3 ? m or more, and has a ferrite area ratio of 60% or more. In addition, as an example of high strength steel sheet that achieves hole conformability and expandability, plt 2 describes a high strength steel sheet that is excellent in hole conformability and expandability containing c, si, cu, and mn in The predetermined mass% further contains at least one of al, ni, mo, cr, v, b, ti, nb, ca and mg, and has a ferritic phase hardness of hv 150 to 240, has a ratio of residual austenite volume in the sheet structure of 2 to 20%, and exhibits a tensile strength of 600 to 800 mpa. plt 3 describes, as an example of high strength cold rolled steel sheet for work use that is excellent in fatigue characteristics, a high strength cold rolled steel sheet for work use that is excellent in fatigue characteristics which is comprised of sheet steel containing c: 0.05 to 0.30%, cu: 0.2 to 2.0%, and b: 2 to 20 ppm and having a microstructure comprised of a volume ratio of 5 % and more and 25% or less of residual austenite and ferrite and bainite and having cu present in the ferritic phase in the state of particles which are individually cu of a size of 2 nm or less in a solid solution state and / or precipitated state. plt 4 describes, as an example of composite high strength cold rolled steel sheet which is excellent in fatigue characteristics, composite high strength cold rolled steel sheet which is comprised of structural steel sheet ferrite-martensite composite containing c: 0.03 to 0.20%, cu: 0.2 to 2.0%, and b: 2 to 20 ppm and having cu present in the ferritic phase in the state of particles which are comprised of cu individually of a size of 2 nm or less in a solid solution state and / or precipitated state. plt 5 describes, as an example of super high strength steel plate which is excellent in retarded fracture resistance, a super high strength steel plate containing by weight% c: 0.08 to 0.30, si: less than 1.0, min: 1.5 to 3.0, s: 0.010 or less, p: 0.03 to 0.15, cu: 0.10 to 1.00, and ni: 0.10 at 4.00, it has an unavoidable iron balance and impurities, contains one or more martensite, tempered martensite, or bainite structures at a volume ratio of 40% or more, and has a strength of 1180 mpa or more. plt 6 describes, as an example of high strength steel plate that is excellent in press forming and corrosion resistance, a high strength steel plate that is excellent in press forming and corrosion resistance that meets the requirements of c : 0.08 to 0.20%, bs: 0.8 to 2.0%, mn: 0.7 to 2.5%, p: 0.02 to 0.15%, s: 0.010% or less, al: 0.01 to 0.10%, cu: 0.05 to 1.0%, and ni: 1.0% or less, have an unavoidable iron balance and impurities, and satisfy the ratio of the following formula "0 , 4 '(10p + si) / (10c + mn + cu + 0.5ni)? 1.6 "(where, the element notations indicate the respective contents (%)), this steel sheet has residual austenite of 3 to 10% and a tensile strength of 610 to 760 mpa. plt 7 describes, as an example of high strength thin steel plate, one of high strength thin steel having an ingredient composition containing c: 0.05 to 0.3%, si: 2% or less, mn : 0.05 to 4.0%, p: 0.1% or less, s: 0.1% or less, cu: 0.1 to 2%, and si (%) / 5 or more, al: 0 , 1 to 2%, n: 0.01% or less, ni: cu (%) / 3 or more (when cu is 0.5% or less, not necessarily included) and satisfies "si (%) + al ( %)? 0.5 "," mn (%) + ni (%)? 0.5 ", has a structure that contains a volume ratio of 5% or more of residual austenite, and exhibits a tensile strength of 650 at 800 mpa. citation list patent literature plt 1: Japanese patent publication no. 2004-100018a plt 2: Japanese Patent Publication No. 2001-355044a plt 3: Japanese patent publication no. 11-279690a plt 4: Japanese Patent Publication No. 11-199973a plt 5: Japanese Patent Publication No. 08-311601a plt 6: Japanese Patent Publication No. 08-199288a plt 7: Japanese Patent Publication No. Technical Problem A conventional high strength steel plate is hot rolled, pickled, and cold rolled, so it is continuously annealed under predetermined conditions to cause the predetermined crystalline phases to precipitate at predetermined ratios on the plate. steel plate structure and thus obtain high strength and high workability. however, in a low alloy steel with low content of added elements, the phase transformation proceeds rapidly at the time of annealing treatment, to the point that the operating range at which the predetermined crystalline phases can be realized to precipitate at predetermined ratios. becomes narrow and as a result, the high strength steel plate does not become stable in properties and varies in quality. In addition, a conventional high strength steel plate with tensile strength of 900 mpa or more is insufficient in workability. It is desired to improve stretch flangeability and otherwise improve workability. The present invention has been realized in consideration of this situation and aims to provide a high strength steel plate with tensile strength of 900 mpa or more where stretch flangeability is enhanced to improve local deformation capability and where tensile strength Traction can be improved when a high speed tension is actuated, and a production method of it. solution to the problem the inventors, etc. involved in intensive studies on the steel sheet structure and the production method to achieve improved stretch flangeability and increased tensile strength when high speed stress is actuated on the high strength steel sheet. As a result, they have found that by effectively causing cu to precipitate on sheet steel, it is possible to achieve improved stretching flangeability and increased tensile strength when the high speed stress is actuated. Furthermore, they have found that to form this structure, it is sufficient to impart tension to the steel plate during annealing of the steel plate. The invention was carried out as a result of further studies based on the above discovery and is based on the following: (1) a high strength steel sheet which is excellent in conformability containing by weight% c: 0.075 to 0.300%, si: 0.30 to 2.50%, mn: 1.30 to 3.50%, p: 0.001 to 0.030%, s: 0.0001 to 0.0100%, al: 0.005 to 1.500%, cu: 0 , 15 to 2.00%, n: 0.0001 to 0.0100%, and o: 0.0001 to 0.0100%, contain as optional elements ti: 0.005 to 0.150%, nb: 0.005 to 0.150% , b: 0.0001 to 0.0100%, cr: 0.01 to 2.00%, ni: 0.01 to 2.00%, mo: 0.01 to 1.00%, w: 0.01 1.00%, v: 0.005 to 0.150%, and one or more between ca, ce, mg, and rem: total 0.0001 to 0.50%, and have an unavoidable iron balance and impurities, where the Steel plate structure contains a ferritic phase and martensitic phase, a ratio of bcc iron incoherent cu particles is 15% or more relative to the cu particles as a whole, a density of cu particles in the ferritic phase is 1, 0-1018 / m3 or more, and an average particle size of cu particles in the ferritic phase is 2.0 nm or more. (2) high strength steel sheet which is excellent in conformability of (1) characterized in that the structure in a range of 1/8 thickness to 3/8 thickness of high strength steel sheet comprises, by volume fraction, a ferritic phase: 10 to 75%, ferritic-bainitic phase and / or bainitic phase: 50% or less, tempered martensitic phase: 50% or less, fresh martensitic phase: 15% or less, and austenitic phase residual: 20% or less. (3) High strength galvanized steel sheet which is excellent in conformability characterized by comprising (1) or (2) high strength steel sheet on the surface whose galvanized layer is formed. (4) a method of producing high strength steel sheet which is excellent in conformability characterized in that it comprises a hot rolling process of heating a plate containing by weight% c: 0.075 to 0.300%, si: 0.30 to 2.50%, mn: 1.30 to 3.50%, p: 0.001 to 0.030%, s: 0.0001 to 0.0100%, al: 0.005 to 1.500%, cu: 0 , 15 to 2.00%, n: 0.0001 to 0.0100%, o: 0.0001 to 0.0100%, contains as optional elements ti: 0.005 to 0.150%, nb: 0.005 to 0.150%, b: 0.0001 to 0.0100%, cr: 0.01 to 2.00%, ni: 0.01 to 2.00%, mo: 0.01 to 1.00%, w: 0.01 to 1.00%, v: 0.005 to 0.150%, and one or more between ca, ce, mg, and rem: total 0.0001 to 0.50%, and have an unavoidable iron balance and impurities, directly or after once cooling at 1050 ° C or more, rolling with a lower temperature limit of 800 ° C or the transformation point ar3, whichever is greater, and cooling at 500 to 700 ° C temperature and an annealing process of heating the coiled steel sheet by r an average heating rate at 550 to 700 ° C from 1.0 to 10.0 ° C / sec. up to the maximum heating temperature of 740 to 1000 ° c, then cooling by an average cooling rate from the maximum heating temperature to 700 ° c of 1.0 to 10.0 ° c / sec, imparting stress to the plate. steel from the maximum heating temperature to 700 ° C, and cooling by a cooling rate of 700 ° C to bs or 500 ° C from 5.0 to 200.0 ° C / sec. (5) The production method of the high strength steel sheet which is excellent in conformability of (5) above characterized by having a cold rolling process, after the hot rolling process and before the annealing process, stripping the rolled steel plate, then roll it by a tightening torque ratio of a tightening torque ratio of 35 to 75%. (6) the high strength steel plate production method which is excellent in conformability of (4) or (5) above characterized by the fact that the stress is imparted to the steel plate in the annealing process by applying 5 to 50 tension plate to the steel sheet while being flexed once or more in a range that provides an amount of tensile stress at the outermost circumference of 0.0007 to 0.0910, (7) the steel sheet production method of High strength which is excellent in the conformability of (6) above characterized by the fact that bending is performed by pressing the steel plate against a roll with a roll diameter of 800 mm or less. (8) A method of producing high strength galvanized steel sheet which is excellent in conformability characterized by the fact that it produces high strength steel sheet through the method of producing high strength steel sheet of any one between ( 4) to (7) above, then it is electroplated. (9) A method of producing high strength galvanized steel sheet which is excellent in conformability characterized by the fact that it produces high strength steel sheet by the production method according to any one of (4) to (8). ) above after cooling to bs or 500? c, hot dip galvanization is performed. (10) A method of producing high strength galvanized steel sheet which is excellent in conformability according to (9) characterized by the fact that it performs alloy treatment at 470 to 650 ° C after temperature dip galvanization. hot. Advantageous Effects of the Invention In accordance with the present invention, it is possible to provide a high strength steel sheet which guarantees a maximum tensile strength of 900 mpa or higher strength while having excellent stretch flangeability and other conformability and also having excellent tensile properties. High tensile strength. In addition, it is possible to provide a high strength galvanized steel sheet which guarantees a maximum tensile strength of 900 mpa or higher strength that has excellent stretch flangeability and other conformability and also has excellent properties of high tensile strength. Description of embodiments First, the structure of the high strength steel plate of the present invention will be explained. The structure of the high strength steel plate of the present invention is not particularly limited as long as a maximum tensile strength of 900 mpa or greater strength can be guaranteed. for example, the structure may be any one of a martensite single phase structure, a double phase structure comprised of martensite and bainite, a double phase structure comprised of ferrite and martensite, a composite phase structure comprised of ferrite, bainite , and residual austenite and other such structures including ferrite, bainite, martensite, and residual austenite individually or in a composite manner. alternatively, this may be a structure of such structures which further include a perlite structure. The ferritic phase that is included in the high strength steel sheet structure can be any precipitation hardened ferrite, unrecrystallized ferrite as worked, or partial displacement restored ferrite. The steel plate structure of the high strength steel plate of the present invention is preferably comprised in the range 1/8 to 3/8 thickness centered on 1/4 plate thickness by volume fraction ferritic phase. : 10 to 75%, ferritic-bainitic phase and / or bainitic phase: 50% or less, tempered martensitic phase: 50% or less, fresh martensitic phase: 15% or less, and residual austenitic phase: 20% or less. If the high strength steel plate has this steel plate structure, the high strength steel plate having the most excellent conformability is derived. Here, the structure is produced in the range 1/8 to 3/8 thickness, as this structure range can be considered to represent the structure of the steel sheet as a whole. If this sheet steel structure is in the range of 1/8 to 3/8 thickness, it can be judged that the sheet steel as a whole has this structure. The phases that can be included in the steel sheet structure will be explained. Ferritic phase The ferritic phase is a structure that is effective for improving ductility and is preferably contained in the sheet steel structure in a volume fraction of 10 to 75%. the volume fraction of the ferritic phase in the sheet steel structure from the point of view of ductility is more preferably 15% or more, even more preferably 20% or more. the ferritic phase is a soft structure, to sufficiently increase the tensile strength of the steel plate, the volume fraction of the ferritic phase that is contained in the steel plate structure becomes more preferably 65% or less, even more preferably if makes it 50% or less. Ferritic-bainitic phase and / or bainitic phase The ferritic-bainitic phase and / or bainitic phase is a structure with a satisfactory balance of strength and ductility and is preferably contained in the sheet steel structure in a volume fraction of 10 to 50%. . In addition, the ferritic-bainitic phase and / or bainitic phase is a microstructure that has intermediate resistance to that of a soft ferritic phase and hard martensitic phase and tempered martensitic phase and residual austenitic phase. From the point of view of stretch flangeability, inclusion of 15% or more is more preferred and inclusion of 20% or more is even more preferred. if the volume fraction of the ferritic-bainitic phase and / or bainitic phase increases, the elastic limit becomes larger, so from the point of view of form freezability, the volume fraction of the ferritic-bainitic phase and / or bainitic phase is preferably 50% or less. Tempered martensitic phase The tempered martensitic phase is a structure that greatly increases the tensile strength. From the tensile strength standpoint, the volume fraction of the tempered martensite is preferably 10% or more. If the volume fraction of the quenched martensite that is contained in the sheet steel structure increases, the elastic limit becomes larger, so from the point of view of form freezability, the quenched martensitic phase volume fraction is preferably 50%. or less. Fresh martensitic phase The fresh martensitic phase usually increases the tensile strength. on the other hand, this forms fracture starting points and generally degrades stretch flangeability, so this is preferably limited to a volume fraction of 15% or less. In order to increase the stretch flangeability, it is more preferred to make the volume fraction of the fresh martensitic phase 10% or less, even more preferably 5% or less. Residual austenitic phase The residual austenitic phase greatly increases strength and ductility. on the other hand, this becomes fracture starting points sometimes causes stretch flangeability to deteriorate, so this is preferably limited to a volume fraction of 20% or less. To enhance stretch flangeability, the volume fraction of the residual austenitic phase is preferably 15% or less. To obtain the effect of increasing strength and ductility, the volume fraction of the residual austenitic phase is preferably 3% or more, preferably 5% or more. others the steel plate structure of the high strength steel plate of the present invention may further contain a perlite and / or coarse cementite phase or other structure. however, if the sheet steel structure of high strength sheet steel contains a large amount of perlite and / or coarse cementite phase, the bending capacity deteriorates. therefore, the volume fraction of the perlite and / or coarse cementite phase that is contained in the sheet steel structure is preferably a total of 10% or less, more preferably 5% or less. The volume fractions of the different structures which are contained in the steel plate structure of the high strength steel plate of the present invention can be, for example, measured by the following method: the volume fraction of the residual austenitic phase is obtained by examining the plane parallel to the surface of the sheet steel plate and at 1/4 thickness by x-ray analysis, calculating the area fraction, and considering the value as the volume fraction. The volume fractions of the ferritic phase, ferritic-bainitic phase, bainitic phase, tempered martensitic phase, and fresh martensitic phase that are contained in the sheet steel structure of the high strength steel sheet of the present invention are obtained by obtaining cut samples. sheet thickness cross sections parallel to the direction of rolling as the observed surfaces, polish the observed surfaces, notch them nitally, then examine the range from 1/8 thickness to 3/8 thickness centered on 1/4 thickness from plate using a field emission scanning electron microscope (fe-sem) to measure the area fraction, and considering this value as the volume fraction. then the microstructure of the high strength steel plate of the present invention will be explained. the high strength steel plate microstructure of the present invention should be one where the particle density of cu is ≤ 1.0-1018 / m3, the average particle size of cu particles is 2.0 nm or more, and the ratio of cu particles where cu particles and the surrounding bcc iron are inconsistent with the total cu particles is 15% or more. "bcc iron" is the general term for ferrite, bainite, and bainitic ferrite with crystalline structures of body-centered cubic matrices. If the cu particles are consistent with bcc iron, the resistance is greatly improved. Cu particles that are not consistent with the bcc iron obstruct the development of the displacement substructure in the bcc iron. Along with this, aggregation of displacements at the time of high stress strain becomes difficult, void formation is suppressed, and as a result, stretch flangeability is improved. the particle density of cu is preferably 5.0 - 1018 / m3 or more, more preferably 1.0 - 1019 / m3 or more. fine cu particles easily maintain coherence with bcc iron and are small in contribution to stretch flangeability, so the lower limit of the average particle size of cu particles becomes 2.0 nm or more. the average particle size of the cu particles is more preferably 4.0 nm or more, even more preferably 6.0 nm or more. If the number of cu particles that are inconsistent with bcc iron is less than 15%, the improvement of stretch flangeability becomes insufficient. therefore, the number of cu particles should be 15% or more, preferably 25% or more, more preferably 35% or more. average particle size, coherence, and particle density of cu can be evaluated as follows: a sample is cut from the steel sheet to 1/4 thickness and examined using a high resolution transmission electron microscope (hrtem). electron energy loss (eels) spectroscopy is used to confirm the composition of the cu particles. These are investigated for particle size and consistency with bcc iron. Particle size has become the average particle size of 20 or more particles. In addition, the ratio of precipitates that are inconsistent with bcc iron in the observed particle number was found. Cu particle density is measured by two methods according to the average particle size. If the average particle size is less than 3 nm, a three-dimensional atomic probe (3d-ap) is used to cut and test 1/4 thickness samples of the steel plate. The test is performed until 20 or more cu particles are obtained or until the measured volume exceeds 50000 nm3. Density is obtained by dividing the number of particles by the measured volume. On the other hand, if the average particle size is 3 nm or larger, the number of cu particles in a field of 10000 nm2 at 1? m2 is measured, convergent beam electron diffraction (cbed) is used to measure the particle size. The thickness of the observed part of the test piece is multiplied by the observed area to find the observed volume, and the number of cu particles is divided by the observed volume to find the density of cu particles. The means for measuring the composition, particle size, and coherence of cu particles are not limited to the above techniques. for example, the particles can be observed using a field emission transmission electron microscope (fe-tem) etc. In the following, the ingredient composition of the high strength steel plate of the present invention will be explained. Note that in the following explanation, "%" should mean "% by mass". c: 0.075 to 0.300% c is included to increase the strength of the high strength steel plate. If the c content exceeds 0.300%, the weldability becomes insufficient. From the point of view of weldability, the c content is preferably 0.250% or less, more preferably 0.220% or less. If the c content is less than 0.075%, the strength is reduced and a maximum tensile strength of 900 mpa or more cannot be guaranteed. to increase strength, the c content is preferably 0.090% or more, more preferably 0.100% or more. si: 0.30 to 2.50% si is an element that suppresses the formation of iron-based carbides in the steel plate and is required to increase strength and conformability. if the self content exceeds 2.50%, the steel plate becomes brittle and the ductility deteriorates. From the point of view of ductility, the content itself is preferably 2.20% or less, more preferably 2.00% or less. On the other hand, if the self content is less than 0.30%, a large amount of coarse iron-based carbide forms in the annealing process, and strength and conformability deteriorate. from that point of view, the lower limit of itself is preferably 0.50% or more, more preferably 0.70% or more. min: 1.30 to 3.50% min is added to increase the strength of the steel plate. If the mn content exceeds 3.50%, concentrated parts of thick mn form in the center thickness of the steel plate, brittleness occurs easily, and problems such as cracking of the molten plate occur easily. In addition, if the mn content exceeds 3.50%, the weldability also deteriorates. therefore, the mn content should be 3.50% or less. From the point of view of weldability, the mn content is preferably 3.20% or less, more preferably 3.00% or less. On the other hand, if the mn content is less than 1.30%, soft structures are formed in large quantities during cooling after annealing, so it is difficult to guarantee a maximum tensile strength of 900 mpa or more. therefore, the mn content should be 1.30% or more. to increase strength, the mn content is more preferably 1.50% or more, even more preferably 1.70% or more. p: 0.001 to 0.030% p tends to precipitate in the center of the steel sheet thickness and cause the weld zone to become brittle. If the p content exceeds 0.030%, the weld zone becomes very fragile, then the p content is limited to 0.030% or less. The lower limit of the p content is not particularly limited as long as the effect of the present invention is exhibited. However, if the p content is less than 0.001%, manufacturing costs increase considerably, so 0.001% becomes the lower limit. s: 0.0001 to 0.0100% s has a detrimental effect on weldability and fabricability at the time of casting and at the time of hot rolling. consequently, the upper limit of s content becomes 0.0100% or less. It binds to mn to form coarse mns that reduces ductility and stretch flangeability, so 0.0050% or less is preferred, while 0.0025% or less is more preferred. The lower limit of s content is not particularly limited as long as the effects of the present invention are exhibited. However, if the s content is less than 0.0001%, manufacturing costs increase considerably, so 0.0001% becomes the lower limit. al: 0.005 to 1,500% al suppresses the formation of iron-based carbides and increases the strength and conformability of the steel plate. If the al content exceeds 1,500%, the weldability becomes unsatisfactory, then the upper limit of the al content becomes 1,500%. From the point of view of weldability, the al content is preferably 1,200% or less, more preferably 0,900% or less. al is also an element that is effective as a deoxidizing material, but if the al content is less than 0.00
公开号:BR112014001589B1
申请号:R112014001589
申请日:2012-07-27
公开日:2019-01-08
发明作者:Minami Akinobu；Murasato Akinobu；Kawata Hiroyuki；Azuma Masafumi；Maruyama Naoki；Yonemura Shigeru；Kuwayama Takuya
申请人:Nippon Steel & Sumitomo Metal Corp；
IPC主号:

专利说明:

Invention Patent Descriptive Report for HIGH-RESISTANCE STEEL SHEET AND EXCELLENT HIGH-RESISTANCE GALVANIZED STEEL SHEET IN CONFORMABILITY AND PRODUCTION METHODS OF THE SAME.
FIELD OF TECHNIQUE [001] The present invention relates to a high-strength steel sheet and a high-strength galvanized steel sheet that are excellent in conformability and methods of producing them.
BACKGROUND OF THE TECHNIQUE [002] In recent years, there has been an increase in demands for greater strength in the steel sheet that is used for automobiles etc. In particular, for the purpose of increasing collision safety, etc., a high-strength steel sheet with a tensile strength limit of 900 MPa or more is also used. This high-strength steel sheet is economically formed in large volumes by press work in the same way as mild steel sheet and is used as structural elements.
[003] However, recently, together with the rapid increase in strength of high-strength steel sheet, particularly in high-strength steel sheet with a tensile strength limit of 900 MPa or more, a problem has arisen that conformability it is becoming insufficient and the work is accompanied by local deformation such as stretch formability that is becoming difficult. Furthermore, when a high-speed tension force acts on a steel material, there is a problem that the fracture mode could easily change from ductile fracture to embrittlement fracture.
[004] In the past, as an example of the technique of hardening a steel material, a high-strength steel material that has been hardened by charging Cu with satisfactory precipitation has been known.
Petition 870180147442, of 11/01/2018, p. 4/66
2/54
PLT 1 describes a high-strength steel material of the Cu precipitation-hardened type that contains C, Si, P, S, Al, N, and Cu in predetermined ranges, contains one or both of Mn: 0.1 to 3, 0% and Cr: 0.1 to 3.0%, has a (Mn + Cr) / Cu of 0.2 or more, and has a balance of iron and unavoidable impurities, has an average crystal grain size of 3 pm or more, and has a ferrite area ratio of 60% or more.
[005] Furthermore, as an example of high strength steel sheet that achieves hole formability and expandability, PLT 2 describes a high strength steel sheet that is excellent in hole formability and expandability that contains C, Si, Cu, and Mn in% of predetermined mass, additionally contains at least one between Al, Ni, Mo, Cr, V, B, Ti, Nb, Ca, and Mg, and has a hardness of the ferritic phase of Hv 150 to 240, has a volume ratio of residual austenite in the plate structure of 2 to 20%, and exhibits a tensile strength of 600 to 800 MPa.
[006] PLT 3 describes, as an example of high strength cold rolled steel sheet for work use that is excellent in fatigue characteristics, a high strength cold rolled steel sheet for work use that is excellent in fatigue characteristics which is comprised of steel plate containing C: 0.05 to 0.30%, Cu: 0.2 to 2.0%, and B: 2 to 20 ppm and which has a microstructure comprised of a ratio volume of 5% or more and 25% or less of residual austenite and ferrite and bainite and which has Cu present in the ferritic phase in the state of particles that are comprised of Cu individually of a size of 2 nm or less in a solution state solid and / or precipitated state.
[007] PLT 4 describes, as an example of high strength cold rolled steel sheet of composite structure which is excellent in fatigue characteristics, a high cold rolled steel sheet
Petition 870180147442, of 11/01/2018, p. 5/66
3/54 resistance of composite structure which is comprised of steel sheet of composite structure of ferrite-martensite containing C: 0.03 to 0.20%, Cu: 0.2 to 2.0%, and B: 2 to 20 ppm and which has Cu present in the ferritic phase in the state of particles which are comprised of Cu individually of a size of 2 nm or less in a state of solid solution and / or precipitated state.
[008] PLT 5 describes, as an example of super high strength steel sheet which is excellent in delayed fracture resistance, a super high strength steel sheet containing, by weight%, C: 0.08 to 0 , 30, Si: less than 1.0, Mn: 1.5 to 3.0, S: 0.010 or less, P: 0.03 to 0.15, Cu: 0.10 to 1.00, and Ni: 0.10 to 4.00, has a balance of iron and unavoidable impurities, contains one or more structures of martensite, tempered martensite, or bainite structures in a volume ratio of 40% or more, and has a strength of 1180 MPa or more.
[009] PLT 6 describes, as an example of high strength steel sheet which is excellent in press forming and corrosion resistance, a high strength steel sheet which is excellent in press forming and corrosion resistance which satisfies the C requirements: 0.08 to 0.20%, Si: 0.8 to 2.0%, Mn: 0.7 to 2.5%, P: 0.02 to 0.15%, S: 0.010% or less, Al: 0.01 to 0.10%, Cu: 0.05 to 1.0%, and Ni: 1.0% or less, has a balance of iron and unavoidable impurities, and satisfies the ratio of the following formula 0.4 <(10P + Si) / (10C + Mn + Cu + 0.5Ni) <1.6 (where, the element notations indicate the respective contents (%)), this steel sheet has residual austenite 3 to 10% and a tensile strength of 610 to 760 MPa.
[0010] PLT 7 describes, as an example of high strength thin steel plate, one of high strength thin steel that has an ingredient composition that contains C: 0.05 to 0.3%, Si: 2% or
Petition 870180147442, of 11/01/2018, p. 6/66
4/54 less, Μη: 0.05 to 4.0%, P: 0.1% or less, S: 0.1% or less, Cu: 0.1 to 2%, and Si (%) / 5 or more, Al: 0.1 to 2%, N: 0.01% or less, Ni: Cu (%) / 3 or more (when Cu is 0.5% or less, not necessarily included) and satisfies Si ( %) + AI (%)> 0.5, Mn (%) + Ni (%)> 0.5, has a structure that contains a volume ratio of 5% or more of residual austenite, and exhibits tensile strength from 650 to 800 MPa. LIST OF QUOTES
PATENT LITERATURE [0011] PLT 1: Japanese Patent Publication No. 2004-100018A [0012] PLT 2: Japanese Patent Publication No. 2001-355044A [0013] PLT 3: Japanese Patent Publication No. 11-279690A [0014 ] PLT 4: Japanese Patent Publication No. 11-199973A [0015] PLT 5: Japanese Patent Publication No. 08-311601A [0016] PLT 6: Japanese Patent Publication No. 08-199288A [0017] PLT 7: Publication Japanese Patent No. 05-271857A
SUMMARY OF THE INVENTION
TECHNICAL PROBLEM [0018] A conventional high strength steel plate is hot rolled, pickled, and cold rolled, then continuously annealed under predetermined conditions to cause the predetermined crystalline phases to precipitate at predetermined ratios in the plate structure steel and thus achieve high strength and high work ability.
[0019] However, in a low alloy steel with low levels of added elements, the phase transformation proceeds quickly at the time of annealing treatment, to the point that the operational range in which the predetermined crystalline phases can be carried out to precipitate at predetermined reasons it becomes narrow and, as a result, the high strength steel sheet does not become stable in properties and varies in quality.
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5/54 [0020] In addition, a conventional high strength steel plate with tensile strength of 900 MPa or more is insufficient in workability. It is desired to improve the flangeability by stretching and otherwise to improve workability.
[0021] The present invention was carried out in consideration of this situation and aims to provide a high strength steel sheet with tensile strength of 900 MPa or more where stretch flangeability is improved to improve local deformation capacity and where tensile strength can be improved when a high speed tension is actuated, and a method of producing it.
SOLUTION TO THE PROBLEM [0022] Inventors, etc. involved in intensive studies on the steel sheet structure and the production method to obtain the improvement of stretching flangeability and increased tensile strength when the high speed tension is actuated on the high strength steel sheet. As a result, they found that to make Cu precipitate efficiently on steel plate, it is possible to obtain improved flangeability by stretching and increased tensile strength when the high speed tension is actuated. Furthermore, they found that to form this structure, it is sufficient to tension the steel sheet during the annealing of the steel sheet.
[0023] The invention was carried out as a result of further studies based on the above discovery and is based on the following:
(1) A sheet of high-strength steel that is excellent in conformability that contains, by weight%, C: 0.075 to 0.300%, Si: 0.30 to 2.50%, Mn: 1.30 to 3.50 %, P: 0.001 to 0.030%, S: 0.0001 to 0.0100%, Al: 0.005 to 1.500%, Cu: 0.15 to 2.00%, N: 0.0001 to
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0.0100%, and Ο: 0.0001 to 0.0100%, contains, as optional elements, Ti: 0.005 to 0.150%, Nb: 0.005 to 0.150%, B: 0.0001 to 0.0100%, Cr: 0.01 to 2.00%, Ni: 0.01 to 2.00%, Mo: 0.01 to 1.00%, W: 0.01 to 1.00%, V: 0.005 to 0.150%, and one or more between Ca, Ce, Mg, and REM: total 0.0001 to 0.50%, and has a balance of iron and unavoidable impurities, in which the steel plate structure contains a ferritic phase and a martensitic phase, a Cu particle ratio inconsistent with bcc iron is 15% or more compared to Cu particles as a whole, a density of Cu particles in the ferritic phase is 1.0x10 ¹⁸ / m ³ or more, and an average particle size of Cu particles in the ferritic phase is 2.0 nm or more.
(2) The high strength steel sheet which is excellent in formability of (1) characterized by the fact that the structure in a range from 1/8 thick to 3/8 thick of the high strength steel sheet comprises, by volume fraction, a ferritic phase: 10 to 75%, ferritic-bainitic phase and / or bainitic phase: 50% or less, tempered martensitic phase: 50% or less, fresh martensitic phase: 15% or less, and austenitic phase residual: 20% or less.
(3) Galvanized steel sheet of high strength which is excellent in conformability characterized by comprising the high strength steel sheet of (1) or (2) on the surface whose galvanized layer is formed.
(4) A method of producing high-strength steel sheet which is excellent in conformability, characterized by the fact that it comprises a hot rolling process of heating a plate containing, by weight%, C: 0.075 to 0.300%, Si: 0.30 to 2.50%, Mn: 1.30 to 3.50%, P: 0.001 to 0.030%, S: 0.0001 to 0.0100%, Al: 0.005 to 1.500%, Cu: 0 , 15 to 2.00%, N: 0.0001 to 0.0100%, O: 0.0001 to 0.0100%, contains, as optional elements, Ti: 0.005 to 0.150%, Nb: 0.005 to 0.150%, B: 0.0001 to 0.0100%, Cr: 0.01 to 2.00%,
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Ni: 0.01 to 2.00%, Mo: 0.01 to 1.00%, W: 0.01 to 1.00%, V: 0.005 to 0.150%, and one or more between Ca, Ce, Mg , and REM: total 0.0001 to 0.50%, and has a balance of iron and unavoidable impurities, directly, or after cooling once, to 1050 ° C or more, lamination with a lower temperature limit of 800 ° C or the transformation point Ar3, whichever is greater, and cooling to 500 to 700 ° C in temperature and an annealing process to heat the rolled steel sheet by an average heating rate to 550 to 700 ° C of 1, 0 to 10.0 ° C / sec. up to the maximum heating temperature of 740 to 1000 ° C, then cooling by an average cooling rate from the maximum heating temperature to 700 ° C of 1.0 to 10.0 ° C / sec, giving tension to the plate. steel from the maximum heating temperature to 700, and cooling by a cooling rate of 700 ° C to the Bs point or 500 ° C from 5.0 to 200.0 ° C / sec.
(5) The production method of the high-strength steel sheet which is excellent in formability of (5) above characterized by having a cold rolling process, after the hot rolling process and before the annealing process, of stripping the rolled steel sheet, then laminate it at a tightening torque rate of a tightening torque rate of 35 to 75%.
(6) The method of producing high strength steel sheet which is excellent in formability of (4) or (5) above characterized by the fact that the stress is given to the steel sheet in the annealing process when applying 5 to 50 MPa of tension to the steel plate while it is flexed once or more in a range that provides an amount of tensile strength in the outer circumference of 0.0007 to 0.0910, (7) The steel plate production method of high strength which is excellent in conformability of (6) above characterized by the fact that bending is performed when pressing the steel sheet
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8/54 against a roll with a roll diameter of 800 mm or less.
(8) A method of producing high-strength galvanized steel sheet that excels in conformability characterized by the fact that it produces high-strength steel sheet using the method of producing high-strength steel sheet from anyone in between ( 4) to (7) above, then it is subjected to electroplating.
(9) A method of producing high-strength galvanized steel sheet that is excellent in conformability characterized by the fact that it produces high-strength steel sheet using the production method according to any of (4) to (8 ) above after cooling to Bs or 500 ° C, hot dip galvanizing is carried out.
(10) A method of producing high-strength galvanized steel sheet which is excellent in conformability according to (9) characterized by the fact that it performs the treatment of alloy at 470 to 650 ° C of temperature after galvanizing by immersion at hot.
ADVANTAGE EFFECTS OF THE INVENTION [0024] In accordance with the present invention, it is possible to provide a high strength steel sheet that guarantees a maximum tensile strength of 900 MPa or higher strength while having excellent stretch flangeability and other conformability and also has excellent properties of high tensile strength. In addition, it is possible to provide a high-strength galvanized steel sheet that guarantees a maximum tensile strength of 900 MPa or higher strength that has excellent stretch flangeability and other conformability and also has excellent properties of high tensile strength.
DESCRIPTION OF MODALITIES
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9/54 [0025] First, the structure of the high strength steel sheet of the present invention will be explained. The structure of the high strength steel sheet of the present invention is not particularly limited as long as a maximum tensile strength of 900 MPa or greater strength can be guaranteed.
[0026] For example, the structure can be any one between a single phase structure of martensite, a double phase structure comprised of martensite and bainite, a double phase structure comprised of ferrite and martensite, a composite phase structure comprised of ferrite, bainite, and residual austenite and other such structures that include ferrite, bainite, martensite, and residual austenite in an individual or compound manner. Alternatively, this can be a structure of these structures that also includes an expert structure.
[0027] The ferritic phase that is included in the structure of the high-strength steel sheet can be any precipitation-hardened ferrite, non-recrystallized ferrite as worked, or partially discorded restored ferrite.
[0028] The steel plate structure of the high-strength steel plate of the present invention is preferably comprised of, in the range of 1/8 to 3/8 thickness centralized at 1/4 of the plate thickness, by volume fraction , ferritic phase: 10 to 75%, ferritic-baitic phase and / or bainitic phase: 50% or less, tempered martensitic phase: 50% or less, fresh martensitic phase: 15% or less, and residual austenitic phase: 20% or less. If the high strength steel sheet has this sheet steel structure, the high strength steel sheet which has a more excellent formability is derived.
[0029] Here, the structure is produced in the range of 1/8 to 3/8 thickness, as this structure range can be considered to re
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10/54 present the structure of the steel sheet as a whole. If this steel plate structure is in the range of 1/8 to 3/8 thick, it can be considered that the steel plate as a whole has this structure.
[0030] The phases that can be included in the steel sheet structure will be explained.
FERRITIC PHASE [0031] The ferritic phase is a structure that is effective in improving ductility and is preferably contained in the steel plate structure in a volume fraction of 10 to 75%. The volume fraction of the ferritic phase in the steel plate structure, from the point of view of ductility, is more preferably 15% or more, even more preferably 20% or more. The ferritic phase is a soft structure, to sufficiently raise the tensile strength of the steel sheet, the volume fraction of the ferritic phase that is contained in the steel sheet structure becomes more preferably 65% or less, even more preferably if makes 50% or less.
FERRITIC-BAINITIC PHASE AND / QU BAINITIC PHASE [0032] The ferritic-bainitic phase and / or bainitic phase is a structure with a satisfactory balance of strength and ductility and is preferably contained in the steel sheet structure in a volume fraction of 10 to 50%. In addition, the ferritic-bainitic phase and / or bainitic phase is a microstructure that has an intermediate resistance to that of a soft ferritic phase and hard martensitic phase and tempered martensitic phase and residual austenitic phase. From the point of view of stretch flangeability, the inclusion of 15% or more is more preferred and the inclusion of 20% or more is even more preferred. If the volume fraction of the ferritic-bainitic phase and / or bainitic phase increases, the elastic limit becomes greater, then from the point of view of shape freezing, the volume fraction of the ferritic-bainitic phase and / or bainitic phase is preferably 50% or less.
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TEMPERED MARTENSITIC PHASE [0033] The tempered martensitic phase is a structure that greatly increases the tensile strength. From the point of view of tensile strength, the volume fraction of the tempered martensite is preferably 10% or more. If the volume fraction of the tempered martensite that is contained in the sheet steel structure increases, the elastic limit becomes greater, then from the point of view of shape freezing, the volume fraction of the tempered martensitic phase is preferably 50% or less.
FRESH MARTENSITIC PHASE [0034] The fresh martensitic phase generally increases the tensile strength. On the other hand, this forms fracture starting points and generally degrades stretch flangeability, so this is preferably limited to a volume fraction of 15% or less. To increase the flangeability by stretching, it is more preferred to make the volume fraction of the fresh martensitic phase 10% or less, even more preferably 5% or less.
RESIDUAL AUSTENITIC PHASE [0035] The residual austenitic phase greatly increases strength and ductility. On the other hand, this becomes the starting point of fracture sometimes causes stretching flangeability to deteriorate, so this is preferably limited to a volume fraction of 20% or less. To increase stretch flangeability, the volume fraction of the residual austenitic phase is preferably 15% or less. To obtain the effect of increasing strength and ductility, the volume fraction of the residual austenitic phase is preferably 3% or more, it is preferably 5% or more.
OTHERS [0036] The steel plate structure of the high strength steel plate of the present invention may also contain a pearlitic and / or
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12/54 thick cementite phase or other structure. However, if the steel plate structure of high strength steel plate contains a large amount of pearlitic phase and / or thick cementite phase, the flexural capacity deteriorates. Therefore, the volume fraction of the pearlitic phase and / or thick cementite phase that is contained in the steel sheet structure is preferably a total of 10% or less, more preferably 5% or less.
[0037] The volume fractions of the different structures that are contained in the steel plate structure of the high strength steel plate of the present invention can be, for example, measured by the following method:
[0038] The volume fraction of the residual austenitic phase is obtained by examining the plane parallel to the surface of the steel sheet plate and in 1/4 of thickness by X-ray analysis, calculating the area fraction, and considering the value as the volume fraction.
[0039] The volume fractions of the ferritic phase, ferritic-baitic phase, bainitic phase, tempered martensitic phase, and fresh martensitic phase that are contained in the steel plate structure of the high strength steel plate of the present invention are obtained by obtaining samples with cross sections of sheet thickness parallel to the lamination direction as the observed surfaces, polish the observed surfaces, notch them by Nital, then examine the range from 1/8 thick to 3/8 thick centered at 1/4 thick plate using a field emission scanning electron microscope (FE-SEM) to measure the area fraction, and considering this value as the volume fraction.
[0040] Then, the microstructure of the high strength steel sheet of the present invention will be explained.
[0041] The microstructure of the high-strength steel plate of the present invention must be one where the density of particles of
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Cu is> 1.0x10 ¹⁸ / m ³ , the average particle size of the Cu particles is 2.0 nm or more, and the Cu particle ratio where the Cu particles and the surrounding bcc iron are inconsistent in the Cu particles Total cu is 15% or more.
[0042] Bcc iron is the general term for ferrite, bainite, and bainitic ferrite with centered body cubic crystalline structures. If the Cu particles are consistent with bcc iron, the resistance is greatly improved. Cu particles that are not coherent with bcc iron obstruct the development of the discrepancy substructure in bcc iron. Along with this, the aggregation of discrepancies at the time of major strain deformation becomes difficult, the formation of voids is suppressed, and as a result, stretching flangeability is improved.
The Cu particle density is preferably 5.0x10 ¹⁸ / m ³ or more, more preferably 1.0x10 ¹⁹ / m ³ or more.
[0044] Fine Cu particles easily maintain consistency with bcc iron and are small in contribution with stretching flangeability, so the lower limit of the average particle size of Cu particles becomes 2.0 nm or more. The average particle size of the Cu particles is more preferably 4.0 nm or more, even more preferably 6.0 nm or more.
[0045] If the number of Cu particles that are inconsistent with bcc iron is less than 15%, the improvement of the flangeability by stretching becomes insufficient. Therefore, the number of Cu particles must be 15% or more, it is preferably 25% or more, more preferably it is 35% or more.
[0046] The average particle size, coherence, and density of the Cu particles can be assessed as follows: [0047] A sample is cut from the steel sheet to 1/4 thickness and is examined using a microscope electronic transmission
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14/54 are high resolution (HRTEM). Electron energy loss spectroscopy (EELS) is used to confirm the composition of Cu particles. These are investigated for particle size and consistency with bcc iron. The particle size has become the average particle size of 20 or more particles. In addition, the ratio of precipitates that are inconsistent with bcc iron in the number of particles observed was found.
[0048] The density of Cu particles is measured by two methods according to the average particle size. If the average particle size is less than 3 nm, a three-dimensional atomic probe (3D-AP) is used to cut and test samples of 1/4 thick steel plate. The test is performed until 20 or more Cu particles are obtained or until the measured volume exceeds 50000 nm ³ . The density is obtained by dividing the number of particles by the measured volume. On the other hand, if the average particle size is 3 nm or greater, the number of Cu particles in a field of 10000 nm ² at 1 pm ² is measured, the converged beam electron diffraction (CBED) is used to measure the thickness of the observed part of the test piece, this is multiplied by the observed area to find the observed volume, and the number of Cu particles is divided by the observed volume to find the density of Cu particles.
[0049] The means for measuring the composition, particle size, and coherence of the Cu particles are not limited to the above techniques. For example, particles can be observed using a field emission transmission electron microscope (FE-TEM) etc.
[0050] In the following, the ingredient composition of the high strength steel plate of the present invention will be explained. Note that in the following explanation,% must mean% by mass.
C: 0.075 to 0.300%
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15/54 [0051] C is included to increase the strength of the high strength steel plate. If the C content exceeds 0.300%, the welding capacity becomes insufficient. From the point of view of the weldability, the C content is preferably 0.250% or less, more preferably 0.220% or less. If the C content is less than 0.075%, the strength is reduced and a maximum tensile strength of 900 MPa or more cannot be guaranteed. To increase strength, the C content is preferably 0.090% or more, more preferably 0.100% or more.
Si: 0.30 to 2.50% [0052] Si is an element that suppresses the formation of iron-based carbides in the steel plate and is required to increase strength and conformability. If the Si content exceeds 2.50%, the steel sheet becomes brittle and the ductility deteriorates. From the point of view of ductility, the Si content is preferably 2.20% or less, more preferably 2.00% or less. On the other hand, if the Si content is less than 0.30%, a large amount of carbides based on coarse iron forms in the annealing process, and the strength and conformability deteriorate. From that point of view, the lower limit of Si is preferably 0.50% or more, more preferably 0.70% or more.
Mn: 1.30 to 3.50% [0053] Mn is added to increase the strength of the steel sheet. If the Mn content exceeds 3.50%, concentrated parts of thick Mn form in the center thickness of the steel plate, embrittlement occurs easily, and problems such as cracking of the molten plate occur easily. In addition, if the Mn content exceeds 3.50%, the welding capacity also deteriorates. Therefore, the Mn content must be 3.50% or less. From the point of view of the welding capacity, the Mn content is preferably 3.20% or less, more
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16/54 ferably 3.00% or less. On the other hand, if the Mn content is less than 1.30%, soft structures are formed in large quantities during cooling after annealing, then it becomes difficult to guarantee a maximum tensile strength of 900 MPa or more. Therefore, the Mn content must be 1.30% or more. To increase strength, the Mn content is more preferably 1.50% or more, even more preferably 1.70% or more.
P: 0.001 to 0.030% [0054] P tends to precipitate in the center of the steel sheet thickness and cause the weld zone to become weak. If the P content exceeds 0.030%, the weld zone becomes very fragile, so the P content is limited to 0.030% or less. The lower limit of the P content is not particularly limited as long as the effect of the present invention is exhibited. However, if the P content is less than 0.001%, the manufacturing costs increase considerably, then 0.001% becomes the lower limit.
S: 0.0001 to 0.0100% [0055] S has a detrimental effect on weldability and workability at the time of casting and when hot rolling. Consequently, the upper limit of the S content becomes 0.0100% or less. S binds to Mn to form coarse MnS that reduces ductility and stretch flangeability, so 0.0050% or less is preferred, while 0.0025% or less is more preferred. The lower limit of the S content is not particularly limited as long as the effects of the present invention are exhibited. However, if the S content is less than 0.0001%, the manufacturing costs increase considerably, then 0.0001% becomes the lower limit.
Al: 0.005 to 1.500% [0056] Al suppresses the formation of carbides based on iron and au
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17/54 increases the strength and conformability of the steel sheet. If the Al content exceeds 1,500%, the welding capacity becomes unsatisfactory, then the upper limit of the Al content becomes 1,500%. From the point of view of the weldability, the Al content is preferably 1,200% or less, more preferably 0.900% or less. Al is also an element that is effective as a deoxidizing material, however if the Al content is less than 0.005%, the effect as a deoxidizing material is not sufficiently obtained, then the lower limit of the Al content becomes 0.005% or more . To obtain sufficiently the deoxidation effect, the amount of Al preferably becomes 0.010% or more.
N: 0.0001 to 0.0100% [0057] N forms thick nitrides that cause ductility and stretch flangeability to deteriorate, so the content should be kept low. If the N content exceeds 0.0100%, this trend becomes more noticeable, then the N content becomes 0.0100% or less. In addition, N becomes a cause of hole formation at the time of welding, so the lower the content the better. The lower limit of the N content is not particularly adjusted as long as the effect of the present invention is exhibited. However, if the N content becomes less than 0.0001%, the manufacturing costs increase considerably, then 0.0001% becomes the lower limit value.
O: 0.0001 to 0.0100% [0058] O forms oxides that cause ductility and stretch flangeability to deteriorate, so the content should be kept low. If the O content exceeds 0.0100%, the deterioration of flangeability by stretching becomes noticeable, then the O content becomes 0.0100% or less. The O content is preferably 0.0080% or less, more preferably 0.0060% or less. The lower limit of the O content is not particularly limited as long as the effect of this
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18/54 vention is displayed. However, if the O content is less than 0.0001%, the manufacturing costs increase considerably, then 0.0001% becomes the lower limit.
Cu: 0.15 to 2.00% [0059] Cu is an important element in the present invention. Cu is present in steel as fine particles. Cu particles that are coherent or semi-coherent with the surrounding bcc phase in particular increase the strength of the steel sheet. Cu particles that are inconsistent with the surrounding bcc iron in particular suppress the formation of discordant substructures within the steel plate to then increase conformability. In the present invention, to sufficiently obtain the effect of the Cu particles, the Cu content must become 0.15% or more. The Cu content is preferably 0.30% or more, more preferably 0.40% or more. On the other hand, if the Cu content exceeds 2.00%, the welding capacity is compromised, then the Cu content becomes 2.00% or less. From the point of view of the weldability, the Cu content is preferably 1.80% or less, more preferably 1.50% or less.
[0060] The strength of the high steel sheet of the present invention can also contain, as needed, the following elements:
Ni: 0.01 to 2.00% [0061] Ni suppresses the embrittlement that occurs due to the addition of Cu in the high temperature region, so it can be deliberately added for the purpose of improving productivity. To achieve this effect, the Ni content must become 0.01% or more. Becoming 0.05% or more is more preferred, while becoming 0.10% or more is even more preferred. If the Ni content exceeds 2.00%, the welding capacity is compromised, then the Ni content becomes 2.00% or less.
Ti: 0.005 to 0.150%
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19/54 [0062] Ti is an element that contributes to the increase of the resistance of the steel plate through precipitation hardening, fine grain hardening by suppressing the growth of ferrite crystal grains, and hardening by discrepancy through suppression of recrystallization. If the Ti content exceeds 0.150%, the precipitation of carbonitrides increases the formability deteriorates, then the Ti content becomes 0.150% or less. From the point of view of conformability, the Ti content is more preferably 0.100% or less, even more preferably 0.070% or less. In order to sufficiently obtain the effect of increased resistance by Ti, the Ti content must become 0.005% or more. To increase the strength of the steel sheet, the Ti content is preferably 0.010% or more, more preferably 0.015% or more.
Nb: 0.005 to 0.150% [0063] Nb is an element that contributes to the increase in the strength of the steel plate through precipitation hardening, fine grain hardening by suppressing the growth of ferrite crystal grains, and hardening by disagreement through suppression of recrystallization. If the Nb content exceeds 0.150%, the precipitation of carbonitrides increases and the formability deteriorates, then the Nb content becomes 0.150% or less. From the point of view of conformability, the Nb content is more preferably 0.100% or less, even more preferably 0.060% or less. In order to sufficiently obtain the effect of increased resistance by Nb, the Nb content must become 0.005% or more. To increase the strength of the steel sheet, the Nb content is preferably 0.010% or more, more preferably 0.015% or more.
V: 0.005 to 0.150% [0064] V is an element that contributes to increase the strength of the steel sheet through precipitation hardening, endu
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20/54 fine grain retention by suppressing the growth of ferrite crystal grains, and hardening by disagreement through suppression of recrystallization. If the V content exceeds 0.150%, the precipitation of carbonitrides increases and the formability deteriorates, then the content becomes 0.150% or less. To obtain sufficiently the effect of the increase in resistance by V, the content must be 0.005% or more.
B: 0.0001 to 0.0100% [0065] B is an element that suppresses the phase transformation at a high temperature and is effective in increasing resistance and can be added in place of part of C and / or Mn. If the B content exceeds 0.0100%, workability while hot is compromised and productivity drops, then the B content becomes 0.0100% or less. From the point of view of productivity, the B content is preferably 0.0050% or less, more preferably 0.0030% or less. To obtain sufficiently greater resistance to B, the B content must be 0.0001% or more. To sufficiently increase the strength of the steel sheet, the B content is preferably 0.0003% or more, more preferably 0.0005% or more.
Mo: 0.01 to 1.00% [0066] Mo is an element that suppresses the phase transformation at a high temperature and is effective in increasing resistance and can be added in place of part of C and / or Mn. If the Mo content exceeds 1.00%, workability while hot is compromised and productivity drops, then the Mo content becomes 1.00% or less. To obtain sufficiently greater resistance by Mo, the content must be | 0.01% or more.
W: 0.01 to 1.00% [0067] W is an element that suppresses the phase transformation at a high temperature and is effective in increasing resistance and can be added in place of part of C and / or Mn. If the W
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21/54 der 1.00%, workability while hot is compromised and productivity drops, so the W content becomes 1.00% or less. To obtain sufficiently greater resistance by W, the content must be 0.01% or more.
Cr: 0.01 to 2.00% [0068] Cr is an element that suppresses the phase transformation at a high temperature and is effective in increasing resistance and can be added in place of part of C and / or Mn. If the Cr content exceeds 2.00%, workability while hot is compromised and productivity drops, then the Cr content becomes 2.00% or less. To obtain sufficiently greater resistance for Cr, the content must be 0.01% or more.
[0069] One or more between Ca, Ce, Mg, Zr, Hf, and REM: Total 0.0001 to 0.5000% [0070] Ca, Ce, Mg, and REM are elements that are effective in improving conformability. One or more can be added. If the content of one or more elements that are selected from Ca, Ce, Mg, and REM exceeds a total of 0.5000%, ductility is likely to be compromised, then the total content of the elements is 0.5000 % or less. To obtain sufficiently the effect of improving the formability of the steel sheet, the total content of the elements must be 0.0001% or more. From the point of view of conformability, the total content of the elements is preferably 0.0005% or more, more preferably 0.0010% or more.
[0071] REM is an abbreviation for rare earth metal and indicates the elements that belong to the series of lantanoids. In the present invention, REM or Ce is generally added as a Mischmetal. Sometimes, elements of the lantanoid series other than La or Ce are contained in a composite way. Furthermore, even when elements of the lantanoid series instead of La and Ce are included
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22/54 with unavoidable impurities, the effects of the present invention are exhibited. Furthermore, even when La or Ce metal is added, the effects of the present invention are exhibited.
[0072] Above, the composition of ingredients of the present invention has been explained, however as long as it is in a range that does not compromise the properties of the steel sheet of the present invention, for example, elements except the essential added elements can also be included as impurities that are derived from the starting materials.
[0073] The high strength steel sheet of the present invention can also be a high strength galvanized steel sheet on the surface of which a galvanized layer or galvanized layer by annealing is formed. By forming a galvanized layer on the surface of the high-strength steel sheet, a steel sheet that has excellent corrosion resistance is derived. Furthermore, by forming a galvanized layer by annealing on the surface of the high-strength steel sheet, a steel sheet that has excellent resistance to corrosion and that has excellent adhesion to the coating is derived.
[0074] In the following, the production method of the high strength steel sheet of the present invention will be explained.
[0075] To produce the high-strength steel plate of the present invention, first, a plate having the aforementioned composition of ingredients is melted. Like the plate that is used for hot rolling, for example, it is possible to use a continuously molten plate that is produced by a thin plate melter etc. For the production method of the high-strength steel sheet of the present invention, it is referred to use a process such as continuous direct casting (CC-DR) where the steel is melted, then immediately hot rolled.
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23/54 [0076] The heating temperature of the plate in the hot rolling process must be 1050 ° C or more. If the heating temperature of the plate is low, the finish laminating temperature drops below the Ar3 point. As a result, the two-phase lamination of the ferritic phase and the austenitic phase is derived, so the hot-rolled sheet structure becomes an irregular mixed grain structure. The irregular structure is not eliminated even after the cold rolling and the annealing process and, therefore, the ductility and the bending capacity deteriorate. In addition, if the finish rolling temperature drops, the rolling load increases and rolling becomes difficult or shape defects are likely to be caused on the steel sheet after rolling. The upper limit of the heating temperature of the plate is not particularly adjusted as long as the effect of the present invention is exhibited, however it is not economically preferred to adjust the heating temperature to an excessively high temperature, so the upper limit of the heating temperature of the plate is preferably 1350 ° C or less.
[0077] The Ar3 point can be calculated using the following formula: Ar ₃ (° C) = 901-325xC + 33xSi-92x (Mn + Ni / 2 + Cr / 2 + Cu / 2 + Mo / 2) + 52xAI [0078 ] In the above formula, C, Si, Mn, Ni, Cr, Cu, Mo, and Al are the contents of the different elements (% by mass).
[0079] The finishing lamination temperature of the hot lamination becomes greater than 800 ° C or the Ar ₃ point as the lower limit and 1000 ° C as the upper limit. If the finish rolling temperature is less than 800 ° C, the rolling load at the time of finishing rolling becomes high, rolling becomes difficult, and shape defects are likely to be caused in the hot rolled steel sheet that is obtained after lamination. If the finishing laminating temperature is lower than the Ar ₃ point, a la
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24/54 hot mining becomes the two-layer region rolling of the ferritic and austenitic phases and the hot rolled steel sheet structure will sometimes become an irregular mixed grain structure.
[0080] The upper limit of the finishing laminating temperature is not particularly adjusted as long as the effect of the present invention is exhibited, however if the finishing laminating temperature becomes excessively high, to guarantee this temperature, the heating temperature of the plate it must become excessively high. Therefore, the upper limit temperature of the finishing laminating temperature is preferably 1000 ° C or less.
[0081] The steel sheet after rolling is rolled at 500 to 700 ° C. If the winding of the steel sheet is carried out at a temperature exceeding 700 ° C, the oxides that are formed on the surface of the steel sheet increase excessively in thickness and the stripping capacity deteriorates. To improve the pickling capacity, the winding temperature is preferably 680 ° C or less, more preferably 660 ° C or less. If the winding temperature becomes less than 500 ° C, the hot rolled steel sheet becomes excessively high in strength and cold rolling becomes difficult. From the point of view of reducing the weight of the load in cold rolling, the winding temperature is preferably 550 ° C or more. 600 ° C or more is more preferred.
[0082] The rolled steel sheet is preferably cooled by a cooling rate of 25 ° C / hour or less. This will promote Cu precipitation.
[0083] The hot-rolled steel sheet produced in this way is pickled. Due to pickling, the oxides on the steel sheet surface can be removed. This is important from the point of enhancing the chemical convertibility of high-strength steel sheet.
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25/54 cold-rolled strength of the final product or hot-dip coating capacity of cold-rolled steel sheet for use in hot-dip galvanized or galvanized steel sheet. Stripping can be just a single treatment or it can be divided into a plurality of treatments.
[0084] The pickled steel sheet can be supplied as it is for the annealing process, however when cold rolling it at a tightening torque rate of 35 to 75%, a steel sheet with a high precision of thickness and shape excellent is obtained. If the tightening torque ratio is less than 35%, it is difficult to keep the shape flat and the final product becomes unsatisfactory in ductility, then the tightening torque ratio becomes 35% or more. If the tightening torque rate exceeds 75%, the cold rolling load becomes very large and cold rolling becomes difficult. Thereafter, the upper limit of the tightening torque rate becomes 75%. The number of rolling steps and the tightening torque rate of each step are not particularly prescribed as long as the effect of the present invention is displayed.
[0085] Next, the obtained hot-rolled steel sheet or cold-rolled steel sheet is subjected to the annealing treatment.
[0086] First, the steel sheet was heated by an average heating rate of 550 to 700 ° C from 1.0 to 10.0 ° C / sec., Preferably 2.0 to 5.0 ° C / sec. , up to the maximum heating temperature. The maximum heating temperature is 740 to 1000 ° C. Due to this treatment, the crystalline structure of the Cu precipitates formed in the previous hot rolling process becomes a fcc (cubic reticule with centered face). Part of the Cu precipitates that produced a fcc at that point of time dissolves in austenite and / or ferrite in the heating process and maintains the regular fcc structure in the subsequent cooling process, so it can be used as a precipitatePetition 870180147442, from 11/01 / 2018, p. 28/66
26/54 of Cu incoherent with bcc iron.
[0087] If the maximum heating temperature is less than 740 ° C, carbides based on thick iron remain undissolved in the steel plate and act as fracture starting points, then the formability is considerably degraded. To reduce the remaining undissolved iron-based carbides, the maximum heating temperature is preferably 760 ° C or more. If the maximum heating temperature exceeds 1000 ° C, the Cu particles melted during heating and the number of Cu particles that are inconsistent with bcc iron become smaller, then the stretch flangeability deteriorates. To make a large number of Cu particles inconsistent with bcc iron, the maximum heating temperature is preferably 970 ° C or less, more preferably 950 ° C or less.
[0088] Then, the steel sheet is cooled by an average cooling rate from the maximum heating temperature at 700 ° C of 1.0 to 10.0 ° C / sec. Furthermore, in the region of maximum heating temperature temperature at 700 ° C, the steel sheet is supplied with deformation. As the method of providing deformation, for example, it is possible to use the method of applying tension of 5 to 50 MPa while flexing one or more times in a range that provides a tensile strain in the outermost circumference of 0.0007 to 0.0910 Because of this, it is possible to recently promote the formation of Cu precipitate nuclei that are coherent or semi-coherent with the surrounding bcc phase. The flexed steel sheet can be flexed backwards.
[0089] If the stress that is applied to the steel sheet is less than 5 MPa, the precipitation of Cu particles is sometimes not sufficiently promoted. To promote the precipitation of Cu particles and increase conformability further, the stress is more preferably 10
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MPa or more, even more preferably 15 MPa or more. If the tension exceeds 50 MPa, the steel sheet may deform plastically and the shape cannot be maintained.
[0090] If the amount of deformation is less than 0.0007, a sufficient formation of cores does not occur and the formability deteriorates easily. From the point of view of conformability, the amount of deformation is preferably 0.0010 or more. If the amount of strain exceeds 0.0910, the shape is not maintained, so the amount of strain is preferably 0.0910 or less. To maintain the shape of the steel sheet, the amount of deformation is more preferably 0.0500 or less, even more preferably 0.0250 or less.
[0091] The thickness of the steel plate is preferably 0.6 mm to 10.0 mm. If the thickness is less than 0.6 mm, the shape of the steel plate can sometimes not be maintained. If the thickness exceeds 10.0 mm, the temperature inside the steel sheet becomes difficult to control. [0092] Bending can be performed, for example, by applying tension while pressing against a roller. The diameter of the roll is preferably 800 mm or less to obtain a sufficient amount of deformation. In addition, if a roll with a diameter of less than 50 mm is used, the maintenance costs of the installation increase, so the roll diameter of 50 mm or more is preferred.
[0093] After that, the steel sheet is cooled from 700 ° C to the point Bs (initial temperature of transformation of bainite) or 500 ° C by a cooling rate of 5.0 to 200.0 ° C / Mon. Bainite or bainitic ferrite begins to form at a temperature below the Bs point, so the cooling rate can also be reduced. Even at a temperature higher than the point Bs, if 500 ° C or less, the ferrite does not grow much, then the cooling rate can be reduced. The Bs point can be calculated using the following formula:
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Bs (° C) = 820-290C / (1-VF) -37Si-90Mn-65Cr-50Ni + 70AI [0094] In the formula above, VF is the volume fraction of ferrite, while C, Mn, Cr, Ni, Al, and Si are the addition amounts of these elements (% by mass).
[0095] Note that it is difficult to directly measure the volume fraction of the ferritic phase during the production of high-strength steel sheet, so in the present invention, a small part of the cold-rolled steel sheet is cut before displacing the sheet through the continuous annealing line, that small part is annealed by the same temperature history as the case of moving it through the continuous annealing line, the change in the volume of the ferritic phase of the small part is measured, the result is used to calculate a numerical value, and that value is used as the volume fraction VF of the ferrite. This measurement can be performed using the result of the first measurement operation when the steel sheet is produced under the same conditions. The value does not have to be measured every time. The measurement is performed again when the production conditions change a lot. Naturally, it is also possible to observe the microstructure of the steel sheet actually produced and feed back the results for production the next time.
[0096] The annealed steel sheet is kept at 250 to 500 ° C for 60 to 1000 seconds to form hard structures, then it is cooled to room temperature. After cooling to room temperature, the steel sheet can be cold rolled by 0.05 to 3.00% for the purpose of correcting the shape.
[0097] The annealed steel sheet can be galvanized to obtain a cold rolled steel sheet. Furthermore, during cooling from the maximum heating temperature to room temperature, for example, after cooling to 500 ° C or after maintenance, it can be immersed in a galvanizing bath to obtain a
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29/54 hot-dip galvanized steel sheet. After immersing the steel sheet in the galvanizing bath, it can be treated for connection in a range of 470 to 650 ° C. In addition, a film comprised of P oxides and / or composite oxides containing P can be formed. EXAMPLES [0098] The plates that have the chemical ingredients (compositions) from A to AL that are shown in Tables 1 and 2 were melted, then immediately after the function they were hot rolled, cooled, rolled, and pickled under the conditions that are shown in Tables 3 to 5. After that, Experiments 4, 9, 14, 19, 25, 29, 87, and 90 left the steel sheets rolled as they were, while the other experiments cold rolled these under the conditions that are described in Tables 3 to 6 after blasting. After that, an annealing process was applied under the conditions that are shown in Tables 7 to 10 to obtain the steel plates from Experiments 1 to 114.
[0099] Note that, Experiment 102 is an example in which the upper limit of the amount of Cu is exceeded. The results of the weldability test conducted after hot rolling were unsatisfactory, so subsequent tests were suspended.
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Table 1
O Bulk% | | 0.0021 I uncle o | 0.0015 I 05 o o o o | 0.0018 | OO O o ‘ | 0.0013 | | 0.0029 | | 0.0013 | | 0.0018 | CM s O o | 0.0032 | 3 o o o | 0.0025 1 | 0.0029 | CO o o o | 0.0008 | | 0.0018 | | 0.0005 | | 0.0022 | | 0.0004 | | 0.0010 | | 0.0034 | | 0.0016 | | 0.0008 | tico o o o ~ | 0.0012 I | 0.0006 | | 0.0005 | CNr- 3 05 CN 05 you- CO CN CC505 CO you- CN CN you- you- 3 05 you- 10 05 CO 05 05 O CNAND CO CO CO CO CO CN 3 CN 3 CO 10 CO CN CO 3 10 CN 00 CO8 10 CO 8 8O 05 05 05 05 05 r> O 05 05 05 05 05 05 05 05 05 05 05 05 05 05 05E φ O O O O O O O O O O O O O O O O O O O O O O O O O O O O OO O O O O O O O O O O O O O O O O O O O O O O O O O O O Oo ^ · CO ω ω CO m CN O CN CN CO O CN CO CO CO CO 00 CN 00 COCOC0 CO 3 10COCN you- 05 < AND CN 10 CO3 CO you- IO IO CO CN CN CN CO CO 108 00 C0 CN CO 3 CO CO CN O O O O O O O O O O CN O O CO O O O OO O 10 O O O OE φ O O O O O O O O O O «- O O O O O O O O O O O O O O O O O© ** %m 05CO CO COCN CO you- 05 10 05CO 05 10 00 00CO you- 05 CO 00IOyou- 10AND 05 CO 05 05 CN 3 CN CN CO 05 CN3 CO 10 CN3 00CO 1005 CO CN CN ω 05 05 05 05 05 05 05 05 05 05 05 05 05 05 05 05 05 05 05 05 0505 05 05 05 E Φ O O O O O O O O O O O O O O O O O O O O O O O O O O O O OO O O O O O O O O O O O O O O O O O O O O O O O O O O O OSP iCN 00 05 10 r- you- io O CO CO 05 you-O you- 10 00 10 CO CO OCO CO 05 COAND 0505 05 050505 05 05 05 05 0505 05 05 O O O O O O O O O O O O O O O O O O O O O O O O O O O O OE φ O O O O O O O O O O O O O O O O O O O O O O O O O O O O Oθ '* pasta 10 CN CO CN CO io 05 s | - 0505 05 00 you- 00 00 05 O you-CN CN’Φ 30505IO you- you- CO 00 CN CN O you- 00 CO O s | -00CN 10 you- you- CO you- 00 00% inCN CN CN CN CN CN CNCNCN CN CN CN1AND 10 CO 1 ^ 3 CM 3 10 you- 3 CO 10 05 you- CO 05 10 00 CO COO you- 05 CO CO00 10 ΙΟΙ ΓΓ » you- 00 CO CO 10 CO O CO you- you- 10 IO 05 you-CM CO IO CO CM you- 10 O 05 O ° JANDOOO OO * " O O O O CM O O O OOo1XP σ ' % CD you- 05 3 OCM CM you- CO CO C0you- 05 you- 00 C0 3 3 0500 CO CM 05 you-AND 00 00 CO IO 00 CM O CO O O CM 05 00 00 CO CM CO CM CO CO O O O 05 OO OCM CMCM CM O OCM CM O OE φ O O O O O O O O O O O O O O O O O O O O O O O O O O O o1 Oθ 'ç Od) X Lll çΦAND < CO O Q LU LL O X"3 k: -1 2 z O CL The there. ω 1- Ξ) > 5 X > N AA AB □ V
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Table 1 Continuation
LO 01 you- 01 CO8 CXI 00 LOL Π π r> O n LOL 01 π r> r> r> Π Π π O O O O O O O O O O O O O O O O O O m m05 CO CXI 00 you- 01 CO CO 8you- 00 LO CO CO n π π π Π Π laughs n O O O O O O O O O O O O O O O O O O CO 10 CXI σι CO you- IOCXI O CXICO Tf O IO O O O CXI O O you- CO CO O O O O O O OO you-05 O 00 10 you- CO CO CXI CO CXI CXI3CO CO C5 Π LOL LOL LOL LOL Π 05 O O O O O O O O O O O O O O O O O O 05 00 CXI Ttyou- 00 00LOL LOL LOL LOL 05O O O O O O O O O O O O O O O O O OB- O LO CXI 03 O CXI CO00 00 00 CO CO O 00o1 CXI CXICXICXI r- 00 CO CO 05 05 05 CM 05 05 05 O 05 00COCO O O O CM 04 | 00 O 05 00 00 you- CO O 05 r- O 05 01 CO T— OCM O OCM O O O O O O O O O n III II 0 T < ^- 'i1 < < < < < <
> c > c > c > c > c > c > c > c > c > c > C > c > c > c > c > c > c > c > c ώώ ώ ώ ώ moan ώ ώ ώ ώ ώ ώ | REM | % in large scale M— I % in large scale N % in large scale O) z % in large scale10.0016 |ΦO % in large scale CO8O o (0 O % in large scale | 0.0019 | > % in large scale 10,152 | | Mo | % in large scale CXI o| o, io | 3rd % in large scale 03θ ' | 0.56 | CO o * s o * 04 θ ' 0.32 | 10.41 | 5 θ ' | 0.28 | | 0.18 | CO o | 89‘0 | | 0.55 | O CM 8 θ ' 8 θ ' 0.57 | | 8S‘0 | z % in large scale M- 00LO o | 0.50 | 0.30 | 0.09 | ο o * CO oO* | 99‘0 | B. Tiθ ' | 89‘0 | Tf8 θ ' 0.59 | | 66’0 | k_O % in large scale B-CO o * LO COO It's the' m % in large scale 10.0024 | 10,0005 |1 Nb | % in large scale| 0.040 |10,007 | i— % in large scale | 0.040 | The cT| 990‘0 | 10,009 | Experiment < Cfl O Q LU l L 0 T"3lz O 0. σ tr ω
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Table 2 (continued)
> c > c > c > c > c > c > c QAND8i3 Q E 8 ώ QAND8 Q E 8 ώ QAND8 Q E 8 ώ > c > c > c > c > c > c ώ ώ ώ ώ ώώ ώώ 10.0024 |10.0015 |10.0021 | | 0.0015 | 10.0012 | o o o o s o o | 80‘0 | | 88'01 | 0.34 | | 69'01 σ> st o O | 99’01 10.00 | CD Siθ ' | 0.41 | LO Siθ ' 10.12 | οι CO cnI GO CXI θ ' | 0.19 | the CN θ ' 5 θ ' 0.37 | co st θ ' co CN Mo * 0.30 | | 1.04 | | 0.39 | 0.57 | 03 cq CN o * CNO | 0.39 | LO StO O) co * 00 siθ ' co ’ CN COO 55 θ ' CN b * θ ' CN CO 3 θ 'LO o ’ Oo o o * | 0.0044 | GO o o ” | 0.056 |10.025 | O o ’1- Z3 > 5 X > N 2 5 | AC | 5LL<5 < 5 *
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Table 3
33/54
| 'AUI | 'AUI | 'AUI inv. | QAND8 | 'AUI | 'AUI | 'AUI | 'AUI Q E 8 ώ | 'AUI | 'AUI > c | 'AUI QAND8 | 'AUI | 'AUI | 'AUI inv. | Ex. Comp. | > _ç E.g. inv. | Ex. Comp. | E.g. inv. | E.g. inv. | >C ώ >C ώ > c > c Ex. Comp. | | Ex. | Ex. | Ex. | Ex. | Ex. | Ex. | Ex. | Ex. | Ex. | Ex. ώ | Ex. | Ex. | Ex. | Ex. | Ex. Cold rolling rate O*· 1 50 | I 50 | I 50 | O I 50 | I 29 | I 29 | I 2t- | O CO I 50 | I 50 | 03 CO O I 50 | I 40 | The co The co O I ov | I 50 | I 50 | I 50 | I 50 | OO I 32 | I 50 | I 50 | Cooling rate after cooling ° C / sec LO The CM LO 03The CM PM co co LOIΜΊ CO LO r ^. CM CO 00 PM LO co the PM The CM 00- 03 Μ 03 PM 03 CO Temp. cooling 1 1LO0310 00 LOCO COLO O3 00 LO co LO3 I 562 | co3 CO CO co 3CO I 579 | the the co LOAND O00 LO co00 LO I 537 | 1 ew I 03 COLO O CO CO LO CO co00 LO 03 THE CO 03POO LO03 LO CN CO CO I fr29 | CO LO LO CO CO CO I 581 | Temp, hot rolling end 1 □ »1 1003 03 | 668 | | 892 | I 232 | | 896 | | 868 | | 955 | | 688 | co03 | 996 | | 912 | o o 03 03 | 941 | | 988 | PM03 | 901 I O03 | 928 | | 948 | | 891 | | 965 | | 949 | | 918 | | 921 | | 962 | | 096 | | 893 | | 968 | Ar3 transformation point 1 ° 1 1 | I | I | I W- | I 741 | | 999 | Co co co Co co co Co co co CO CO co I 602 | I 709 | 03 The r ^. 1 709 1 I 709 | | 645 | | 645 | I sw | | 645 | | 645 | | 664 | | 664 | | 664 | | 664 | | 664 | I 21-9 I I 3L9 I I 3L9 I CMs I 3L9 | Temp. plate heating 1 0 ° 1 | 1215 | | 1250 | | 1270 | | 1195 | | 1230 | | 1235 | | 1250 | | 1265 | | 1245 | LO | 1175 | | 1190 | O00 | 1205 | O00 | 1260 | | 1270 | | 1240 | | 1260 | | 1195 | | 1270 | | 1250 | | 1250 | | 1175 | O00 | 1215 | | 1245 | | 1285 I | 1225 | | 1260 | Chemical ingredients < < < < < CD £ 0 CD CD CD O O O O O Q Q Q Q Q LU LU LU LU LU LL LL LL LL LL Experiment - CM CO st LO co00 03 O - CM coLO CO00 03 The CM CM I I I I I t-z I LO CM CO CM I I I sz | 03 CM CO
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Table 4
>C ώ > c ώ > c ώ Q E 8 ώ Q E 8 ώ E.g. inv. > c ώ E.g. inv. Q E 8 ώ Q E 8 ώ E.g. inv. > c ώ > c ώ Q E 8 ώ Q E 8 ώ > c ώ > c ώ > c ώ > c ώ E.g. inv. >C ώ > c > C > c ώ > c ώ >C ώ > c ώ > c ώ > c ώ >C ώ Cooling rate after cooling ss CO hs | - r * st O 0 CO The ID s LD The LD s s s ID CO CD CD CD CO s § § s s LD ID ID ID ID Temp. cooling 8 ω O 0 CD CO CM CD the CXJ the CXI CM CO CO 1 ^ CXI CM the CXI CO 00 00 The CXI 01 CXI LD s | - CM COCXI 01 CXI CD 00 the CXI Temp, hot rolling end O0 The CO ID ldCO ld 00CO 00LD 00 the COO00 LD 00ld sCO 0 CO the CO CO δ 3CO dogCO 3 3 LD 0i CO CO 00 CO 00δ The δ 00 COCO 0 COLD 3 LD LD00 LD 0 LDCO CO00 LD LD00 LD CO CXI CO ID0 LD 3 LD Ar3 transformation point O0 00 CD 0i CO0i 00 s CO0i00 CMO) 0i00 COO) O0i hi CO 0i 01 CO 01 LD0000 301 CO01 s01 Oi LD Oi O0Í CXI CO 0Í 00 CO 0Í 30Í LD1 ^03 Hi cxi 0Í 000000 O O 0Í CO 01 80Í 0Í CXI 0Í CM£ 40Í s 301 0ͧ Temp. plate heating O0 O r ^ · o r ^ · o r ^ · o r ^ · δ r ^. r ^ · r ^ · CO r ^ · r ^ · CO r ^ · r *. CO r ^ · r *. CO r ^. r ^ · CO 3CO 3CO 3CO 3CO 3CO r ^ ·00 CO r ^ ·00 CO r ^.00CD LD LD LD LD LD LD LD LD LD CO3 CO3 CO3 O00 CO O00 CO O00CO 3CO 3CO 3CO Chemical ingredients O0 the CO CXJ the LD CXJ LD CO CXJ LD r *. CM LD OCM the LD CXI LD COCXI O00 LD the CXI LD CO o the CXI LD01 ID§ ID LD o the CXI O0i CO CXI LD0Í LD CXJ CXJ LD0Í s CD CXI LD LD CXI CXI LD CO CN LD CN CN o o OJ OOJ Chemical ingredients 0 0 0 0 0 I I I I I"3 "3 "3* * -1 -1 -1 s s s z z z Experiment δ CXI CO POO 3 LD CO POO h * CO 00 CO CD CO O 5 CM CO 5 LD Tj- CO r ^ · 00 Μ ^- 01 Μ ^- the LD δ CM LD CO LD 3 LD LD CO LD r ^ · LD 00 LD 01 LD the CO
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Table 5
E.g. inv. | > c ώ E.g. inv. | E.g. inv. | E.g. inv. | E.g. inv. | > c E.g. inv. | E.g. inv. | E.g. inv. | E.g. inv. | E.g. inv. | E.g. inv. | > c ώ E.g. inv. | E.g. inv. | E.g. inv. | E.g. inv. | E.g. inv. | E.g. inv. | > c E.g. inv. | E.g. inv. | E.g. inv. | E.g. inv. | E.g. inv. | E.g. inv. | > c E.g. inv. | E.g. inv. | Cold rolling rate O*· i w i I w | I w | i w i I w | I w I I 47 | I 29 | I 29 | I 40 | 1 50 | The co The co s The co The co The co The co I 50 | The LO I 50 | I 50 | I 50 | 00 co I 50 | I 50 | O I 50 I I 50 | O Cooling rate after cooling ° C / sec co00 03LOCO CO 'd- CO co 00 I 22 I CXI1 ^ 00 OCXI CXI -CXI CO 00 co O 03 the CXI Temp. cooling 1 0 ° 1 ANDCO I 597 | | 622 | | 614 | I 526 | | 653 | I ws | | 609 | | 530 | | 566 | 1 229 | | 594 | | 564 | ANDCO the co | 566 | 1 582 | | 620 | | 909 | | 618 | | 650 | I 2V9 I I ε / 9 | K-00CD ANDCD | 909 | | 590 | | 583 I | 658 | | 583 | Temp, hot rolling end O0 | 096 | | 945 | | 964 | | 914 | co03 CXIs co3 | 916 | CO0)00 | 891 | AND | 941 | | 606 | I 006 I | 668 | I 226 | | 953 | | 919 | | 933 | | 006 | | 891 | | 956 | | 961 I | 939 | | 963 | | 933 | | 988 | | 920 | | 954 | | 696 | Ar3 transformation point 1 ° 1 | 602 | | 602 | | 602 | | 999 | | 999 | | 999 | | 681 | | 681 | | 681 | | 599 | | 599 | | 599 | | 999 | | 999 | | 999 | | 563 | | 563 | | 563 | | 566 | | 566 | | 566 | xl- xl- xl- r ^. CDCD r ^. CD CD r ^. CDCD CXI0) LO CXI03 LO CXI03 LO Temp. plate heating 1 1 | 1250 | | 1240 | | 1260 | | 1215 | | 1175 | | 1200 | | 1230 | | 1270 | | 1220 | | 1220 | O00 | 1205 | | 1205 | | 1200 | | 1190 | | 1270 | | 1180 | | 1245 | | 1245 | | 1245 | | 1230 | | 1265 | | 1190 | | 1205 | | 1270 | | 1260 | | 1260 | | 1265 I | 1220 | | 1270 | Chemical ingredients O O O CL CL CL σ σ σ A.D Dí tZ I- I- I- Z) Z) Z) > > > £ £ £ X X X Experiment AND CXI co Poo 3 LO CO Poo Γ ** · co 00 co 03 co The r ^.CXI r ^ · CO r ^ ·LO r ^ · co r ^ · r ^ · r ^ · 00 r ^ · 03 r ^ · O00 AND CXI00 co00 s LO00 CD00 00 0000 0300 O03
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Table 6
36/54
E.g. inv. | E.g. inv. | E.g. inv. | E.g. inv. | E.g. inv. | E.g. inv. | QAND8 QAND8 QAND8 QAND8 QAND8 Q E 8 ώ E.g. inv. | E.g. inv. | E.g. inv. | E.g. inv. | E.g. inv. | E.g. inv. | E.g. inv. | E.g. inv. | E.g. inv. | E.g. inv. | E.g. inv. | E.g. inv. | Cold rolling rate O*· | 50 | I 091 £ CO CO CO I 091 I 091 I 091 I 091 I 09 |I 09 | I 091 I 091 I 091 I 091 I 091 I 091 I 09 I 091 I 091 I 091 I 09 | Cooling rate after cooling ° C / sec si- LO CN LO CO 1 ^. CN LOsl- 00 LO CO 00 LO CT CO 00 1 ^ · CT CO LO CO LO Temp. cooling O0 CO 1010 CO CN CO 3CO 3 POO CN CO LO 10 CO 00 CO LO | 009 the CN CO LO O CO 3CO CO00 LO | 909 00 LO LO CN CO | 909 CT CT LO 00 s 0000LO 3LO 0000 LO 3LO Temp, hot rolling end O0 963 | | 918 | | 949 | | 920 | | 9961 | 893 | 926 | | 929 | 933 | | 919 | the CT CNCT | 9881 902 | | 0981 | 894 | | 914 | | 9061 | 920 | LO00 1 ^ OO 902 | oo 902 | Ar3 transformation point O0 | 545 | | 545 | | 545 | 3CO 3CO 3CO CN CO CN | 6991 CNdog CN£ CN£ | 641 | 641 | | 632 | 632 | I 90Z | LO O r ^ · 00 00 CO CO£ | 563 | | 563 | Temp. plate heating O0 | 1230 | | 1210 | | 1185 | | 1230 | | 1255 | | 1215 | LOCN | 1250 | | 1230 | | 1215 | | 1192 | | 1204 | | 1215 | | 1230 | | 1250 | | 1210 | | 1205 | | 1220 | | 1220 | | 1205 | | 1245 | | 1240 | | 1235 | | 1210 I Chemical ingredients > > > N N N s 2 | AC | 5 £ LL< 3 3 5 5 < < 5 | AJ | % % <!Experiment s CN CT CO CT 3 LO CT CO CT l <. CT oo CT CT CT | ioo I O CN O CO o | 104 | I 90l | | 106 | r ^ · o 00 o | 109 | O T- CN CO sl-
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Table 7
Ex, inv, | Ex, inv, | Ex, inv, | Ex, inv, | Q E 8 d > C > c > c > c Q E 8 d > c > c >Ç > c Q E 8 d Ex, inv, | Ex, inv, | Ex, inv, | Ex, inv, | in8> 3 Ex, inv, | Ex, inv, | Q E 8 d Ex, inv, | Ex, inv, | Ex, inv, | Ex, inv, | Ex, inv, | Ex, inv, | QAND8 d Ex, i Ex, i Ex, i Ex, iEx, i ώ ώ Connection process Temp. binding 1 1 1 619 | I Wfr |CO I 523 |Retention process Time 8 tfí | 208 | 1 261 | | 194 | | 186 | 00dog LO I 222 | 00 h- | 296 | Hi00 | 309 | CO Oi CO CN | 109 | I 247 | LO Hi I 210 | 1 202 | | 328 | | 298 | Hi co | 492 | | 224 | I 89V I I 212 | | 182 | 1 576 | | 182 | | 385 | dogCO Second cooling process ScoreBs O0 | 564 | | 568 | CO Ui | 550 | COUi | 550 | | 564 | £ LO | 558 | CO r ^. Ui r ^. CN LO | 535 | 1 ^. CN LO | 536 | CN LO LO r ^ · N ^- | 538 | O) wm | 546 | 909 | CO CO s | - Hi wow Ui ui £ 400 | 494 | CN LO 1 ^. CN LO Oiii 3LO Average cooling rate ω U 0 1 ^ CO The cn I 6.3 | 00co I 10.3 | 00 co CO_ Ν 'wow Poo I S 'ZL · | 00 1 7.9 | 00 co CN dog LO LO CN CO3 I Vsz | 1 28.3 | I 9'ζε | I fr'82 I I 35.5 | I 62.3 | I 76.5 | I 84.9 | 1 2'02 | I 107.3 | 1 36.2 | UiU CN CNC * i S | - 00 sfCO First cooling process Tension tn Q. S 1 st- | the Ui I 50 | I 50 | I st- | LO CO Hi I 50 I LO CO I 40 | 1 50 | st The LO CO CO s I 0t7 I CO CO I ov | LO CN CO LO CO CO LO CN CO The Ui 1 22 | CN 1 ot | Average cooling rate 8 ⁵ <3 0 1 4.0 | 1 2’ε 1 st I ε'ζ | I 2.9 | I 4.0 | I 2’e | I ε‘21 I 9’t- | I 2’t- | 1 2'ε | 1 9'ε | ω CO I 2’2 | LOCNCO ui 1 4.0 | 1 4.1 | CO Ui Ui I 2.7 | CN St I 8’2 | 1 2'ε | 1 2.5 | 1 S‘2 | COI col Heating process Temp, heating O0 CO LO 00 Ui LO 00 0) CO CO r ^. CO 00 CO Ui 00 I 662 I O) oõ oõ I £ 62 I CO o 00 The s LO3 LO CO 00 CO CO 00 I 228 |CO 1 764 | I 062 | 00 |The r ^ l Hi0000 I 262 | -I r ^. the 00 1 799 | I 192 | 00 CN 00 Hi5 1 758 | 00 o 00 Heating rate 1 ° C / sec |Ui I 3.9 | I 3.0 | I 9’ε | COCO00 cn I 4.0 | I 8’t- | st CO COCN st IOC cni I 4.0 | Poo 1 1 I 4.3 | St CN I 4.0 | I 8’2 | COC * i 00C * i HiCN St co ’ HiCN 1 ^ CN COCN HiCN Steel type 1 yo 1 1 yo 1 here I hr | I yo1 ι yo ι ι yo ι Hey at X I yo I I yo I I yo I 0 | HR-GA | i yo ι I yo I I yo I 0 I hr | I yo ι 0 I yo ι I yo ι l yo ι | HR-GA 1 l yo ι X X l yo ι 0 LU l yo ι Chemical ingredients < < < < < CD CD CD CD CD O O O O O Q Q O Q Q LU LU LU LU LU LL LL LL LL LL ExperimentCN CO st LO CO00 Hi OCN CO Ν ' LO CO 1 ^ · 00 σ » I 20 | CN I 22 | CO CN I ÈL ·! CN Ui CO CN r ^ · CN 00 CN 1 62 | CO
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Table 8
>C tí Ex, inv, Ex, inv, Eg how, Ex. With d, Ex, inv, Ex, inv, > c li Ex. With d, Q E 8 d >C li Ex, inv, >C li Q E 8 d Q E 8 d Ex, inv, Ex, inv, Ex, inv, Ex, inv, Ex, inv, Ex, inv, Ex, inv, Ex, inv, Ex, inv, > c Ex, inv, Connection process Temp. binding O0 I 523 IO00 sj- ioRetention process Time 8 ω CO05CN I sz | 00 CO CN I τοε | I ζιε | LO £ POO POO CO05 I Z8L | I 354 | CO o hi CN LO r «-i GO CO I ZZ9 | O05 or LO CO CO O o LOÇN CO I 205 I O cessationthis ScoreBs 1 1 05 LO | 601 | | 605 | | 535 | | 620 | I 433 | I 492 | £Ν ’ | 909 | The LO I 592 | | 589 | 3 co | 593 | I 581 | | 560 | I 6Z9 | | 558 | | 899 | I 562 | 0000LO I 578 | | 569 | I εζ9 | | 489 I I 534 I Second cooler pro Temp. binding 8 ω O 0 1 7'6 | I s' z | I 106.2 | co_I 59.8 | I z'zz | I 79.7 I I 0.6 | LOIO LO I 96.6 | I 17.5 | the 05 I 20.9 | I 16.9 | I 71.6 | I 43.4 | I 36.5 | I 46.6 | 00 to The co COO) 05 0005 " The io I 18.0 I O Tension <Q Q. S the io 05 The CN I 50 | HI I 45 | 05 CO CN I 40 | hi ‘g φE φ col 05 05 O LO CO LO CO I st- | I 07 I LO I 07 | I 24 | LO I 26 | co co O I 45 I First cooling process Average cooling rate 8 <50 CO I I co I Tõ | I 4.3 | I 2.6 | CDω CN st to I ζ'ε | CO sf I Z '7 I CN I z ‘£ | I 7’ε I I z’z I I 7’e | I 4.8 | O05 I 4.0 | I 9'7 | in co CD co I 5.8 I judgment Temp, heating 1 1 | 816 I | 816 | | 810 | I εΐ-θ I I ZI-8 | I 06Z | | 826 | I ZL8 | dog LO dog I 9ZZ | I L6Z | CO05 r ^ · I 786 | | 802 | | 818 | | 819 | | 826 | | 922 | | 922 | I ZL6 | I Z88 | | 832 | | 822 | I L6Z I I 810 I Aqi process Heating rate 8 ω O 0 I 8’Z | COCO I Z'z | I 4.5 | I 7’ε I I ζ'ε I O) I z’z I COCO COI ε'ζ | CO Ν ' COCO I ε'ζ | Poo' I 9'7 | I 8'7 | I 3.0 | I 7'ε | I 4.3 | I 4.0 | I Z’7 | I ε'ζ | I 2.3 I Steel type I to I I to I I 33 | I to I I ao | I ao | I ao | here I ao | there the I to I I ao | 0 LLi I to I I ao | I to I I to II ao | I ao | here I ao | I ao | 0 I ao | I to I Chemical ingredients 0 0 0 0 0 I I I I I"3 "5 "3 4 kí k: —I —I —I Experiment 32 | 33 | I τε LO CO POO I ζε 38 | 05 CO The Ν ’ 5 CN Ν ' CO st 44 | 45 | 46 | I Z7 48 | 03 st The LO LO CN LO co LO 3 55 | 56 I
Petition 870180147442, of 11/01/2018, p. 41/66
39/54
Continuation
> > > > ç ç ç ç li debt debt liH- CO O CO CO LOCO CO CO O) 1 ^. CD r ^ ·CN 00LO LO LO LO ST St LO LO 1 22.1 44, 1 37. 1 ^LO LO CN CN CO CO CDLO st CO CN CN COLO CN O CN CN COCO CO 00 00 CO CO O 00 CN st CO CODí Dí (9 0 O O LU s z z Z r ^ · CO CD O 10 LO LO CO
Ex, inv, | Ex, inv, | > c dl > c dl > c dl > cdl > cdl > cdl > cdl > cdl Ex, inv, | Ex, inv, | Ex, inv, | > cdl Ex, inv, | Ex, inv, | Ex, inv, | > cdl > cdl > c dl > cdl Connection process Temp. binding 0000Ν ’| 999 |Retention process Time 8 to 1 499 1 1 922 1 | 220 | CO CO CO CO CD CO CD | 389 1 5 LO CD LO CD i i I 581 | Poo CD h- | 186 | CD CD | 222 | I 433 | I 258 | | 456 | | 108 I Second cooling process ScoreBs O0 1 ew | 1 £ 6t7 | | 554 | | 539 | 1 ^. CN LO | 568 1 | 508 | CO LO I 513 | | 389 | I I I 4Wz | I εεν | | 455 | I 451 | | 448 | I 523 | I 485 | | 405 | I 487 | CD LO CN Temp. binding ° C / sec 1 fr'ze | 1 36.9 | 1 96.0 | LO co ” LO r < 1 70.8 1 1 53.1 I 3 ' I 55.0 | I 38.8 | I 43.8 | I 40.6 | I 2'2 | 00 LO CD I 9'2 | CD co ” I Z'4 | CO oo ’ CO o I 123.9 I First cooling process Tension <Q0. s 00 1 42 1 1 45 | 1 ^ LO Ν ’ 1 0V I CO CN LO CN The LO LO CN st LO00 LO l · * CN The LO I 40 | I 26 | LO CN I 42 | O CO CN Average cooling rate 8 s 0 1 4.0 |ω CO 1 2.8 | st st ” CD co ” C * 3 co ” CN oo ” I I I 4.0 | CDI L I I 9'2 | I 4'ε |CD co ” poo" st Heating process Temp, firing O0 1 ει.8 | 00 o 00 00s 1,789 | LO001 ^. CO o 00 CN£ 400 AND00 COdog I 6fr2 | I 922 | I 282 | s I 9 ^ 8 I CO co 00 I 492 | I 022 | I 992 I I 692 | I 760 | I 992 | Download rate ° C / sec 1 fr’s 1 1 2.6 | 1 4.9 | 1 4.0 | CO sF CN sF CDCN poo" I 2.5 | CN I tr 'I I 4.0 | ^ t " I 2.9 | I 4.9 | I 2.9 | The co ’ Poo' I 2.7 | I 4'ε | Steel type 1 ho 1 i ho i 0 i ho i Say the Hey I to I Say the I 33 | I HO I I HO I here I HO | I HO | 0 I HO | I HO | 0 I HO | I HO | 0 Chemical ingredients O O O CL CL CL σ σ σ Dí Dí oc CD co CD I- I- I- Z) Z) Z) Experiment AND CN CO POO 3 LO CO POO r ^ · co 00 co CD CO O r ^ ·CN r ^ · co r ^ ·LO r ^ · co r ^ · r ^ · r ^ · 00 r ^ · CD r ^ · O00 s
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Continuation
Ex, inv, | > c ώ > c ώ > c ώ > c ώ > c > c ώ Ex, inv, | > c| 484 | 1 2L9 | O 00 B-0) CN st 03 CO LO CO 00 03 O O B- B- CO CO CN CNLO CO LO CN CN 03 CN O LO LO Or ^. CO CO CO LO s CO 00O CN LO LO LO LO Ν ' LO LO LO LO CN CN 03 Ν ' CN r ^ · LOCO LO CNCN CN CN σ>CN CN CO COLO LO CO O O CO O CN CO CN s | - s | - CNCN00 00 LOLO00 CO CN CO stCN CN CO CO LO O CN 00 r ^. 03 CO CO 00 CNCN r ^. CNO 00 00 00 00 00 r ^. 00 00 O> st st LOLO CN 03 CN CNCN Ν ’ Ν ’ CN CN CO Ν ' CN CO rr rrrr rr eJ tr rr here O O 0 O O tk X O O ± X > > > % X X X CN CO s LO CO r ^ · 00 03 O 00 00 00 00 00 00 00 03
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> c ώ >C ώ >C ώ > c ώ Ex, inv, Ex, inv, Q E 8 ώ Q E 8 d Q E 8 d Q E 8 d Q E 8 d Q E 8 d > ’C li > ’C í > ’C í Connection process O 1 (0 rf 1— § O0 CO03 st 03 CO LO co03 stRetention process TheAnd £ 8 ω 03CO CN CO bCO 0003 sLO O03 CN 5CN sCN The co bbCN 3CO LO bCN co POO bb- Second cooling process Oc o «0- co O0 stLO CN LO CO o LO The LO CN LO 03 CN LO CO CO LO LO03 LO st CN CO 00 co dogLO O5 B- LO O ^ t o 1 (0 &E = φ Φ 1— u 8 ω 0 0 LO co Ν ' CRAZY CO co CN CN Ν 'CO 1 ^. the ’N st5 N CO St0) CN st the CN dog dog 03 co CO CN co CO LO_CO First cooling process The i (DC0 c £ frog0. S LO CN The s | - The Ν ' CO CN 03 CO CN the LO O O LO CO The LO CO CN CN 00 THE(Ü(D E θ £ S c í E 8 <50 LOCN The co COCN COCN The co CNCN 03 co B-_ 00CN COCN co CNCN OCN cn Heating process o “I ac â'8 ® £ 1- ¹⁰ ωO The dog CO CO 00 LO CN 00 CO00 03 b- The steel 00 o 00 03 St 00 st00 00 LO 00 the dog 0303 IR00 LO03 2 c <u S ^E 11 8CO 00 COCN CO co 00 co 00CN poo poo Ν 'CN r ^ co CN co ’ 00CN 03CN CN St co Steel type X o X o eJ X o X o here X o X o X o X o X o X o Hey X o Chemical ingredients > > > N N N s 5 <: LL< Experiment 03 CN03 CO03 3 LO03 CO03 r ^ ·03 oo03 0303 the o O CN O co o 3 LO O
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Continuation
> > > > > > > > > ç ç ç ç ç ç Ç Ç ç ώ ώ ώ ώ ώ dl ώ The 00 co LOLO O03 s | - 0000 00 0300 CO l · - 0003 H- CO00 LO CO co 00 CN CN LO 00 si- st si si 00 B- st LO LO LO LO LO LO st st O 00 LO 03 CN si- LO CN 03 o r · ** CO CN LOLO00 5 LO00 s 00 N O) CN CO 03 00 00 COCNCN CN 00 CN00 LO 0300 CN coCNCNCNCN si- 00 CO O 03 00 st CN LO Γ3 00O03 03 00 00 00 00 00 03 03 CN 03 LOCNSt co st 00 00 00 Ν ' Ν ' st N- 00 0 rrrrrr < rr < LU O 0 O 0 O 0 O 0< < co00 03 OCN 00 st O O O O T— T— T— T—
Petition 870180147442, of 11/01/2018, p. 44/66
42/54 [00100] In the heating process, the steel sheets were heated by the average heating rates described in Table 7 to Table 10 in the range of 550 to 700 ° C up to the maximum heating temperatures described in Table 7 to Table 10 , [00101] After that, in the first cooling process from the maximum heating temperature to 700 ° C, the steel sheets were cooled by the average cooling rates described in Table 7 to Table 10 in the temperature region from the temperature maximum heating at 700 ° C, while applying the stresses that are described in Table 7 to Table 10, in Experiments 1 to 20, a 600 mm radius roller was used to flex the steel sheets six times through a deformation by maximum tensile strength of 0.0020, Similarly, in Experiments 21 to 39, a roller with a radius of 450 was used to flex the steel sheets twice by a maximum tensile strain of 0.0055, in Experiments 41 to 75, a roll of 730 mm radius was used to flex steel sheets seven times by a maximum tensile strain of 0.0010, and in Experiments 76 to 114, a 500 mm radius roll was used to flex steel sheets five times per a maximum tensile strain of 0.0040. The thickness of the steel plate at the moment of bending is 1.2 mm in Experiments 1 to 20, 2.5 mm in Experiments 21 to 39, 0.7 mm in Experiments 41 to 75, and 2.0 mm in Experiments 76 a 114.
[00102] In the second cooling process from 700 ° C to 500 ° C or at point Bs, the steel sheets were cooled by the average cooling rates described in Table 7 to Table 10, then they were additionally cooled from a range of 250 to 500 ° C, were maintained exactly during the times described in Table 7 to Table 10, then they were cooled to room temperature.
[00103] After cooling to room temperature, in Experiments 6 to 20 and 70 to 114, the steel sheets were cold rolled
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43/54 by 0.15%, in Experiment 22, the steel sheet was cold rolled by 1.50%, in Experiment 28, the steel sheet was cold rolled by 1.00%, and in Experiments 31 a 54, the steel sheet was cold rolled by 0.25%.
[00104] Experiments 29, 33, 43, 60, and 69 are examples in which steel sheets are electrolytically laminated after the annealing process to obtain galvanized steel sheets (EG).
[00105] Experiments 13, 54, 57, 63, 75, and 78 are examples in which steel sheets are cooled to 500 ° C or at point Bs in the second cooling process, then are kept in a range of 250 to 500 ° C while being immersed in a galvanizing bath to obtain hot-dip galvanized steel sheets (Gl).
[00106] Experiments 18, 21, 81, and 84 are examples in which steel sheets are kept in a range of 250 to 500 ° C, then immersed in a galvanizing bath, then cooled to room temperature to obtain sheets of hot-dip galvanized steel (Gl).
[00107] Experiments 3, 8, 14, 25, 93, and 96 are examples in which steel sheets are cooled to 500 ° C or at point Bs in the second cooling process, then are kept in a range of 250 to 500 ° C while being kept in a galvanizing bath and are additionally treated for bonding at the temperatures described in order to obtain hot-dip galvanized steel sheets (GA).
[00108] Experiments 38, 48, 51, 66, 72, 87, and 90 are examples in which after the retention treatment in a range of 250 to 500 ° C, the steel sheets are immersed in a galvanizing bath and treated for bonding at the temperatures described to obtain hot-dip galvanized steel sheets (GA). Experiments 38 and 72 are examples where the surfaces of
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44/54 position are provided with films comprised of composite oxides based on P.
[00109] Table 11 to Table 14 provide the results of measuring the fractions of the microstructures of the steel sheets of Experiments 1 to 114 in the range of 1/8 thickness to 3/8 thickness. In the microstructure fractions, the amounts of residual austenite (residual γ) were measured by X-ray diffraction. The rest was found by cutting the sheet thickness cross sections parallel to the lamination direction, polishing them on shiny surfaces, engraving the cross sections by Nital, then examined using a field emission scanning electron microscope (FE-SEM).
Table 11
Experiment Chemical ingredients Steel type Microstructure observation resultsVolume fraction F B BF TM M 7 Residual Others % % % % % % % 1 THE CR 27 16 20 31 2 4 0 E.g. inv. 2 THE CR 28 18 27 21 1 5 0 E.g. inv. 3 THE GA 12 25 23 32 1 6 1 E.g. inv. 4 THE HR 46 15 11 22 0 6 0 E.g. inv. 5 THE CR 33 21 18 19 2 6 1 Ex comp. 6 B CR 32 24 16 23 0 4 1 E.g. inv. 7 B CR 14 30 23 26 0 5 2 E.g. inv. 8 B GA 37 18 12 28 0 5 0 E.g. inv. 9 B HR 37 19 15 24 1 4 0 E.g. inv. 10 B CR 25 22 18 26 2 6 1 Ex comp. 11 Ç CR 23 18 16 30 0 11 2 E.g. inv. 12 Ç CR 21 23 23 23 0 10 0 E.g. inv. 13 Ç Gl 15 31 18 28 0 7 1 E.g. inv. 14 Ç HR-GA 19 25 23 23 0 10 0 Ex inv. 15 Ç CR 33 9 19 27 1 11 0 Ex comp. 16 D CR 52 16 7 15 0 9 1 Ex inv. 17 D CR 21 31 14 21 1 10 2 Ex inv. 18 D Gl 33 24 17 19 0 7 0 Ex inv. 19 D HR 15 29 34 12 0 8 2 Ex inv. 20 D CR 78 0 0 0 0 5 17 Ex comp. 21 AND Gl 40 5 23 22 1 9 0 Ex inv. 22 AND CR 64 7 14 6 0 9 0 Ex inv. 23 AND CR 23 19 28 19 0 11 0 Ex comp. 24 AND CR 45 17 15 12 1 10 0 Ex inv. 25 AND HR-GA 59 4 15 11 0 9 2 Ex inv. 26 F CR 50 31 7 8 0 4 0 Ex inv. 27 F HR 23 43 18 15 1 0 0 Ex inv. 28 F CR 15 41 6 35 2 1 0 Ex inv. 29 F EG 43 19 12 17 0 8 1 Ex inv. 30 F CR 0 48 25 22 0 5 0 Ex comp.
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Table 12
Experiment Chemical ingredients Steel type Microstructure observation resultsVolume fraction F B BF TM M 7 Residual Others % % % % % % % 31 G CR 57 14 7 18 1 2 1 E.g. inv. 32 G CR 46 21 9 21 0 3 0 E.g. inv. 33 G EG 33 34 17 15 0 0 1 E.g. inv. 34 G CR 67 14 2 6 0 3 8 Ex comp. 35 G CR 23 38 14 20 2 2 1 Ex comp. 36 H CR 66 0 8 16 0 10 0 E.g. inv. 37 H CR 53 8 16 13 0 9 1 E.g. inv. 38 H GA 63 4 9 15 1 8 0 E.g. inv. 39 H CR 50 31 5 0 3 4 7 Ex comp. 40 H CR 48 15 12 11 1 11 2 Ex comp. 41 I CR 20 45 12 21 2 0 0 E.g. inv. 42 I CR 32 27 13 25 0 3 0 E.g. inv. 43 I EG 24 29 13 29 1 3 1 E.g. inv. 44 I CR 33 36 9 13 0 2 7 Ex comp. 45 I CR 45 10 6 12 22 5 0 Ex comp. 46 J CR 17 26 15 36 0 6 0 Ex inv. 47 J CR 9 41 22 22 0 5 1 Ex inv. 48 J GA 41 17 10 25 0 6 1 Ex inv. 49 K CR 27 23 14 24 2 10 0 Ex inv. 50 K CR 23 31 6 28 1 11 0 Ex inv. 51 K GA 16 35 13 32 0 4 0 Ex inv. 52 L CR 15 36 17 27 0 2 3 Ex inv. 53 L CR 10 28 13 44 0 4 1 Ex inv. 54 L Gl 36 32 10 19 1 1 1 Ex inv. 55 M CR 48 2 14 20 0 15 1 Ex inv. 56 M CR 11 19 32 20 2 15 1 Ex inv. 57 M Gl 15 0 21 44 0 20 0 Ex inv. 58 N CR 36 8 25 15 1 14 1 Ex inv. 59 N CR 24 23 27 9 1 15 1 Ex inv. 60 N EG 36 0 9 45 1 7 2 Ex inv.
Table 13
Experiment Chemical ingredients Steel type Microstructure observation resultsVolume fraction F B BF TM M 7 Residual Others % % % % % % % 61 O CR 51 21 7 16 1 4 0 Ex inv. 62 O CR 73 9 4 11 0 3 0 Ex inv. 63 O Gl 21 27 19 31 0 2 0 Ex inv. 64 P CR 38 20 10 22 0 9 1 Ex inv. 65 P CR 41 20 9 20 0 8 2 Ex inv. 66 P GA 17 19 9 46 0 9 0 Ex inv. 67 Q CR 34 11 21 26 0 8 0 Ex inv. 68 Q CR 13 22 32 26 0 7 0 Ex inv. 69 Q EG 39 7 15 23 2 11 3 Ex inv. 70 R CR 71 0 5 13 1 10 0 Ex inv. 71 R CR 49 9 11 25 1 5 0 Ex inv. 72 R GA 53 17 10 14 0 6 0 Ex inv. 73 s CR 56 5 9 23 0 7 0 Ex inv. 74 s CR 45 6 18 23 0 7 1 Ex inv. 75 s Gl 39 10 23 21 0 7 0 Ex inv. 76 T CR 63 8 5 15 0 9 0 Ex inv. 77 T CR 21 24 17 30 0 7 1 Ex inv.
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Experiment Chemical ingredients Steel type Microstructure observation resultsVolume fraction F B BF TM M y Residual Others % % % % % % % 78 T Gl 58 9 5 17 0 10 1 E.g. inv. 79 u CR 71 21 2 0 3 3 0 Ex inv. 80 u CR 47 23 12 16 0 0 2 Ex inv. 81 u Gl 74 13 0 9 2 2 0 Ex inv. 82 V CR 18 26 23 18 2 12 1 Ex inv. 83 V CR 32 9 20 24 0 14 1 Ex inv. 84 V Gl 34 23 23 11 0 9 0 Ex inv. 85 w CR 13 36 26 19 0 6 0 Ex inv. 86 w CR 25 23 14 29 0 9 0 Ex inv. 87 w HR-GA 65 4 8 16 1 6 0 Ex inv. 88 X CR 40 20 14 19 3 3 1 Ex inv. 89 x CR 44 7 0 45 2 2 0 Ex inv. 90 x HR-GA 15 32 19 28 0 6 0 Ex inv.
Table 14
Experiment Chemical ingredients Steel type Microstructure observation resultsVolume fraction F B BF TM M y Residual Others % % % % % % % 91 Y CR 35 8 21 24 2 10 0 Ex inv. 92 Y CR 10 19 35 25 0 11 0 Ex inv. 93 Y GA 41 5 29 16 0 8 1 Ex inv. 94 Z CR 54 18 12 10 0 6 0 Ex inv. 95 z CR 25 31 15 20 1 7 1 Ex inv. 96 z GA 25 32 21 16 0 5 1 Ex inv. 97 AA CR 38 16 21 16 1 8 0 Ex comp. 98 AB CR 93 0 4 0 0 0 3 Ex comp. 99 B.C CR 20 46 3 22 0 2 7 Ex comp. 100 AD CR 30 27 25 5 1 0 12 Ex comp. 101 AE CR 37 25 15 13 0 10 0 Ex comp. 102 AF - - - - - - - - Ex comp. 103 AG CR 47 11 18 12 3 8 1 Ex inv. 104 AG GA 35 3 52 5 0 5 0 Ex inv. 105 AH CR 36 11 34 7 0 12 0 Ex inv. 106 AH EG 13 4 34 32 2 15 0 Ex inv. 107 Al CR 20 16 33 27 0 3 1 Ex inv. 108 Al Gl 27 18 37 14 0 1 3 Ex inv. 109 AJ CR 57 10 25 1 3 4 0 Ex inv. 110 AJ Gl 57 0 21 15 0 7 0 Ex inv. 111 AK CR 39 6 33 9 2 10 1 Ex inv. 112 AK GA 51 7 14 18 1 9 0 Ex inv. 113 AL CR 27 51 8 12 0 0 2 Ex inv. 114 AL GA 24 35 10 28 1 2 0 Ex inv.
[00110] Table 15 to Table 18 show the results of observing the precipitates of Cu.
[00111] Samples cut from 1/4 steel sheets were observed for Cu precipitates using a high resolution transmission electron microscope (HRTEM). Electron energy loss spectroscopy (EELS) was used to
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47/54 confirm the composition of the Cu particles. These were investigated for particle size and consistency with bcc iron. The particle size became the average particle size of 25 particles. Furthermore, the reason for the precipitates that are inconsistent with bcc iron in the number of particles that was observed was found.
[00112] In these experiments, there are no test pieces with average precipitate sizes of 3 nm or less, so it is assumed that the average particle size is 3 nm or more, the number of Cu particles in a field of 10000 nm ² to 1 pm ² was measured, the converged beam electron diffraction (CBED) was used to measure the thickness of the observed part of the test piece, this was multiplied by the observed area to find the observed volume, and the number of particles Cu was divided by the observed volume to find the density of Cu particles.
Table 15
Experiment Chemical ingredients Steel type Cu ParticlesDensity Average size Incoherent particle ratio No, / m ³ nm % 1 THE CR 9.9x10 ¹⁸ 7.6 36 Ex, inv, 2 THE CR 1.5x10 ¹⁹ 6.2 28 Ex, inv, 3 THE GA 7.0x10 ¹⁸ 7.2 24 Ex, inv, 4 THE HR 1.6x10 ¹⁹ 7.0 48 Ex, inv, 5 THE CR 1.6x10 ²⁰ 7.0 68 Eg comp, 6 B CR 1.6x10 ²¹ 6.3 96 Ex, inv, 7 B CR 1.3x10 ¹⁹ 7.7 100 Ex, inv, 8 B GA 1.3x10 ¹⁹ 7.8 52 Ex, inv, 9 B HR 1.1x10 ¹⁹ 4.6 80 Ex, inv, 10 B CR 4.2x10 ²¹ 2.4 0 Eg comp, 11 Ç CR 5.5x10 ¹⁸ 8.2 72 Ex, inv, 12 Ç CR 4.6x10 ¹⁸ 5.8 24 Ex, inv, 13 Ç Gl 5.7x10 ¹⁸ 5.5 24 Ex, inv, 14 Ç HR-GA 1.5x10 ¹⁹ 4.2 88 Ex, inv, 15 Ç CR 2.2x1o ²² 16 4 Eg comp, 16 D CR 1.2x10 ²⁰ 5.2 36 Ex, inv, 17 D CR 6.2x10 ¹⁹ 5.7 100 Ex, inv, 18 D Gl 3.7x10 ¹⁹ 6.2 28 Ex, inv, 19 D HR 7.4x10 ¹⁹ 6.6 40 Ex, inv, 20 D CR 3.2x10 ¹⁹ 4.9 100 Eg comp, 21 AND Gl 1.7x10 ¹⁸ 5.1 24 Ex, inv, 22 AND CR 1.6x10 ¹⁸ 4.8 64 Ex, inv, 23 AND CR 1.9x10 ¹⁸ 2.7 4 Eg comp,
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Experiment Chemical ingredients Steel type Cu ParticlesDensity Average size Incoherent particle ratio No, / m ³ nm % 24 AND CR 5.1x10 ¹⁸ 4.7 84 Ex, inv, 25 AND HR-GA 1.1x10 ¹⁸ 5.6 88 Ex, inv, 26 F CR 1.5x10 ¹⁹ 3.6 40 Ex, inv, 27 F HR 5.6x10 ¹⁸ 5.6 44 Ex, inv, 28 F CR 5.7x10 ¹⁸ 5.8 72 Ex, inv, 29 F EG 5.9x10 ¹⁸ 6.2 96 Ex, inv, 30 F CR 6.2x10 ¹⁸ 15 8 Eg comp,
Table 16 Experiment Chemical ingredients Steel type Cu ParticlesDensity Average size Incoherent particle ratio No./m ³ nm % 31 G CR 1.1x10 ¹⁹ 6.8 40 E.g. inv. 32 G CR 1.6x10 ¹⁹ 4.8 20 E.g. inv. 33 G EG 2.0x10 ¹⁹ 4.5 28 E.g. inv. 34 G CR 3.7x10 ¹⁸ 11.8 100 Ex. Comp. 35 G CR 3.9x10 ¹⁷ 5.5 24 Ex. Comp. 36 H CR 2.8x10 ¹⁹ 4.9 56 E.g. inv. 37 H CR 9.0x10 ¹⁹ 3.4 32 E.g. inv. 38 H GA 1.8x10 ¹⁹ 4.3 80 E.g. inv. 39 H CR 2.7x10 ¹⁸ 7.7 28 Ex. Comp. 40 H CR 2.5x10 ¹⁷ 12.6 100 Ex. Comp. 41 I CR 5.7x10 ¹⁸ 5.0 32 E.g. inv. 42 I CR 2.5x10 ¹⁸ 6.3 40 E.g. inv. 43 I EG 3.8x10 ¹⁹ 4.8 84 E.g. inv. 44 I CR 8.9x10 ¹⁷ 8.5 44 Ex. Comp. 45 I CR 1.0x10 ¹⁹ 4.2 32 Ex. Comp. 46 J CR 1.5x10 ¹⁹ 3.4 20 E.g. inv. 47 J CR 2.7x10 ¹⁸ 4.8 64 E.g. inv. 48 J GA 1.2x10 ¹⁸ 3.9 36 E.g. inv. 49 K CR 1.5x10 ²⁰ 5.9 76 E.g. inv. 50 K CR 5.4x10 ¹⁹ 6.9 44 E.g. inv. 51 K GA 6.8x10 ¹⁹ 6.5 84 E.g. inv. 52 L CR 3.7x10 ¹⁹ 7.5 52 E.g. inv. 53 L CR 9.4x10 ¹⁹ 4.1 60 E.g. inv. 54 L Gl 3.0x10 ¹⁹ 8.2 64 E.g. inv. 55 M CR 1.4x10 ¹⁹ 6.0 48 E.g. inv. 56 M CR 7.1x10 ¹⁹ 6.0 40 E.g. inv. 57 M Gl 1.3x10 ²⁰ 5.2 36 E.g. inv. 58 N CR 4.9x10 ¹⁹ 6.8 88 E.g. inv. 59 N CR 1.0x10 ²⁰ 6.6 32 E.g. inv. 60 N EG 1.5x10 ¹⁹ 5.4 60 E.g. inv.
Table 17
Experiment Chemical ingredients Steel type Cu ParticlesDensity Average size Incoherent particle ratio No, / m ³ nm % 61 0 CR 2.0x10 ²⁰ 6.6 96 Ex, inv, 62 0 CR 9.5x10 ¹⁹ 7.6 92 Ex, inv, 63 0 Gl 1.1x10 ²¹ 5.0 68 Ex, inv,
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Experiment Chemical ingredients Steel type Cu ParticlesDensity Average size Incoherent particle ratio No, / m ³ nm % 64 P CR 3.0x10 ¹⁸ 7.3 60 Ex, inv, 65 P CR 5.1x10 ¹⁸ 5.6 76 Ex, inv, 66 P GA 5.3x10 ¹⁸ 4.4 44 Ex, inv, 67 Q CR 1.0x10 ²⁰ 7.0 40 Ex, inv, 68 Q CR 1.9x10 ²⁰ 5.7 72 Ex, inv, 69 Q EG 5.5x10 ²⁰ 4.5 56 Ex, inv, 70 R CR 7.1x10 ¹⁹ 4.8 44 Ex, inv, 71 R CR 2.6x10 ¹⁹ 5.4 72 Ex, inv, 72 R GA 1.7x10 ²⁰ 6.5 56 Ex, inv, 73 s CR 2.6x10 ¹⁹ 6.1 36 Ex, inv, 74 s CR 5.7x10 ¹⁹ 6.0 96 Ex, inv, 75 s Gl 1.8x10 ¹⁹ 7.1 48 Ex, inv, 76 T CR 3.6x10 ²⁰ 6.2 28 Ex, inv, 77 T CR 1.1x10 ²⁰ 9.9 88 Ex, inv, 78 T Gl 1.8x10 ²⁰ 13.9 100 Ex, inv, 79 u CR 3.6x10 ¹⁹ 7.2 76 Ex, inv, 80 u CR 1.7x10 ²⁰ 4.7 68 Ex, inv, 81 u Gl 2.3x10 ²⁰ 3.2 24 Ex, inv, 82 V CR 9.4x10 ¹⁸ 3.6 64 Ex, inv, 83 V CR 3.3x10 ¹⁹ 3.2 68 Ex, inv, 84 V Gl 2.4x10 ¹⁹ 3.4 40 Ex, inv, 85 w CR 3.3x10 ²⁰ 3.4 28 Ex, inv, 86 w CR 1.7x10 ²⁰ 4.8 76 Ex, inv, 87 w HR-GA 4.6x10 ²⁰ 4.3 72 Ex, inv, 88 X CR 2.6x10 ¹⁹ 3.9 28 Ex, inv, 89 X CR 2.1x10 ²⁰ 4.5 60 Ex, inv, 90 X HR-GA 6.8x10 ¹⁸ 3.8 56 Ex, inv,
Table 18
Experiment Chemical ingredients Steel type Cu ParticlesDensity Average size Incoherent particle ratio No, / m ³ nm % 91 Y CR 1.8x10 ²⁰ 3.6 48 Ex, inv, 92 Y CR 2.0x10 ²⁰ 3.9 80 Ex, inv, 93 Y GA 1.0x10 ²¹ 3.5 48 Ex, inv, 94 Z CR 1.3x10 ²⁰ 4.1 100 Ex, inv, 95 z CR 2.9x10 ²⁰ 3.7 36 Ex, inv, 96 z GA 6.5x10 ¹⁹ 3.6 36 Ex, inv, 97 AA CR 0 - - Eg how, 98 AB CR 3.5x10 ¹⁹ 3.6 20 Eg comp, 99 B.C CR 9.4x10 ¹⁹ 3.3 96 Eg comp, 100 AD CR 3.5x10 ¹⁹ 3.6 32 Eg comp, 101 AE CR 2.3x10 ¹⁶ 4.5 44 Eg comp, 102 AF - - - - Eg comp, 103 AG CR 2.0x10 ²⁰ 4.3 52 Ex, inv, 104 AG GA 2.4x10 ²⁰ 3.7 40 Ex, inv, 105 AH CR 3.2x10 ¹⁹ 3.9 36 Ex, inv, 106 AH EG 6.4x10 ¹⁹ 3.5 60 Ex, inv, 107 Al CR 1.0x10 ²⁰ 3.4 24 Ex, inv, 108 Al Gl 9.5x10 ¹⁹ 3.7 84 Ex, inv, 109 AJ CR 1.5x10 ²¹ 4.9 68 Ex, inv, 110 AJ Gl 1.0x10 ²¹ 4.6 36 Ex, inv,
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Experiment Chemical ingredients Steel type Cu ParticlesDensity Average size Incoherent particle ratio No, / m ³ nm % 111 AK CR 1.9x10 ²¹ 4.0 72 Ex, inv, 112 AK GA 1.7x10 ²¹ 4.8 52 Ex, inv, 113 AL CR 2.3x10 ²¹ 3.9 52 Ex, inv, 114 AL GA 2.5x10 ²¹ 4.1 28 Ex, inv,
[00113] Table 19 to Table 22 show the results of evaluating the properties of the steel sheets of Experiments 1 to 114. The tensile test pieces based on JIS Z 2201 were obtained from the steel sheets of Experiments 1 to 114 114 were submitted to tensile tests based on JIS Z 2241 to measure the yield strength (YS), tensile strength (TS), total elongation (EL), and maintain the expansion rate (λ).
Table 19
Experiment Chemical ingredients Steel type Material measurement results TSxEL TSxXYS TS EL λ MPa MPa % % MPa «% MPa «% 1 THE CR 733 935 21 42 19635 39270 E.g. inv. 2 THE CR 668 947 19 53 17993 50191 E.g. inv. 3 THE GA 911 1080 18 37 19440 39960 E.g. inv. 4 THE HR 694 1054 18 51 18972 53754 E.g. inv. 5 THE CR 693 974 9 15 8766 14610 Ex comp. 6 B CR 686 968 18 42 17424 40656 E.g. inv. 7 B CR 889 1058 20 43 21160 45494 E.g. inv. 8 B GA 707 1026 20 39 20520 40014 E.g. inv. 9 B HR 715 985 18 58 17730 57130 E.g. inv. 10 B CR 831 1098 17 23 18666 25254 Ex comp. 11 Ç CR 843 1086 16 42 17376 45612 E.g. inv. 12 Ç CR 952 1253 16 52 20048 65156 E.g. inv. 13 Ç Gl 866 1067 19 64 20273 68288 E.g. inv. 14 Ç HR-GA 926 1174 15 35 17610 41090 Ex inv. 15 Ç CR 857 1142 15 19 17130 21698 Ex comp. 16 D CR 840 1523 12 43 18276 65489 Ex inv. 17 D CR 988 1329 14 38 18606 50502 Ex inv. 18 D Gl 1110 1551 12 35 18612 54285 Ex inv. 19 D HR 1098 1410 13 46 18330 64860 Ex inv. 20 D CR 554 772 3 9 2316 6948 Ex comp. 21 AND Gl 699 1099 18 69 19782 75831 Ex inv. 22 AND CR 563 1125 18 51 20250 57375 Ex inv. 23 AND CR 886 1185 15 16 17775 18960 Ex comp. 24 AND CR 672 1093 17 43 18581 46999 Ex inv. 25 AND HR-GA 569 1105 19 39 20995 43095 Ex inv. 26 F CR 783 1343 14 30 18802 40290 Ex inv. 27 F HR 923 1284 13 47 16692 60348 Ex inv. 28 F CR 1026 1179 14 38 16506 44802 Ex inv. 29 F EG 732 1165 16 50 18640 58250 Ex inv. 30 F CR 1168 1344 9 2 12096 2688 Ex comp.
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Table 20
Experiment Chemical ingredients Steel type Material measurement results TSxEL TSxXYS TS EL λ MPa MPa % % MPa «% MPa.% 31 G CR 552 1075 17 52 18275 55900 E.g. inv. 32 G CR 699 1098 18 44 19764 48312 E.g. inv. 33 G EG 828 1182 14 37 16548 43734 E.g. inv. 34 G CR 452 1007 14 24 14098 24168 Ex. Comp. 35 G CR 823 1092 18 19 19656 20748 Ex. Comp. 36 H CR 643 1305 15 37 19575 48285 E.g. inv. 37 H CR 733 1307 14 35 18298 45745 E.g. inv. 38 H GA 682 1320 13 40 17160 52800 E.g. inv. 39 H CR 649 1055 15 10 15825 10550 Ex. Comp. 40 H CR 717 1197 14 22 16758 26334 Ex. Comp. 41 I CR 885 1184 17 39 20128 46176 E.g. inv. 42 I CR 876 1218 16 38 19488 46284 E.g. inv. 43 I EG 909 1169 15 52 17535 60788 E.g. inv. 44 I CR 721 1080 11 15 11880 16200 Ex. Comp. 45 I CR 675 1369 12 3 16428 4107 Ex. Comp. 46 J CR 879 1047 17 42 17799 43974 E.g. inv. 47 J CR 930 1075 18 39 19350 41925 E.g. inv. 48 J GA 676 984 20 47 19680 46248 E.g. inv. 49 K CR 963 1275 15 42 19125 53550 E.g. inv. 50 K CR 1303 1672 10 28 16720 46816 E.g. inv. 51 K GA 1111 1331 13 39 17303 51909 E.g. inv. 52 L CR 775 963 21 57 20223 54891 E.g. inv. 53 L CR 1053 1140 18 40 20520 45600 E.g. inv. 54 L Gl 684 1024 16 51 16384 52224 E.g. inv. 55 M CR 824 1438 15 31 21570 44578 E.g. inv. 56 M CR 1126 1390 14 39 19460 54210 E.g. inv. 57 M Gl 1306 1457 14 29 20398 42253 E.g. inv. 58 N CR 856 1247 16 36 19952 44892 E.g. inv. 59 N CR 1114 1555 12 30 18660 46650 E.g. inv. 60 N EG 1279 1581 12 49 18972 77469 E.g. inv.
Table 21
Experiment Chemical ingredients Steel type Material measurement results TSxEL TSxXYS TS EL λ MPa MPa % % MPa »% MPa »% 61 O CR 599 1012 17 40 17204 40480 E.g. inv. 62 O CR 393 1071 18 43 19278 46053 E.g. inv. 63 O Gl 898 1090 16 49 17440 53410 E.g. inv. 64 P CR 958 1396 11 36 15356 50256 E.g. inv. 65 P CR 888 1279 15 50 19185 63950 E.g. inv. 66 P GA 1237 1376 14 39 19264 53664 E.g. inv. 67 Q CR 847 1180 16 47 18880 55460 E.g. inv. 68 Q CR 1126 1367 12 40 16404 54680 E.g. inv. 69 Q EG 963 1434 13 26 18642 37284 E.g. inv. 70 R CR 564 1319 13 31 17147 40889 E.g. inv. 71 R CR 792 1234 16 49 19744 60466 E.g. inv. 72 R GA 784 1422 14 39 19908 55458 E.g. inv. 73 s CR 675 1154 18 41 20772 47314 E.g. inv. 74 s CR 769 1112 16 40 17792 44480 E.g. inv. 75 s Gl 722 1019 19 48 19361 48912 E.g. inv. 76 T CR 548 1185 19 39 22515 46215 E.g. inv. 77 T CR 980 1249 14 35 17486 43715 E.g. inv.
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Experiment Chemical ingredients Steel type Material measurement results TSxEL TSxXYS TS EL λ MPa MPa % % MPa «% MPa «% 78 T Gl 663 1338 16 47 21408 62886 E.g. inv. 79 u CR 515 1393 13 38 18109 52934 Ex inv. 80 u CR 827 1349 15 38 20235 51262 E.g. inv. 81 u Gl 430 1218 15 50 18270 60900 Ex inv. 82 V CR 1078 1413 13 36 18369 50868 Ex inv. 83 V CR 904 1294 16 40 20704 51760 Ex inv. 84 V Gl 938 1391 14 37 19474 51467 Ex inv. 85 w CR 942 1181 14 35 16534 41335 Ex inv. 86 w CR 885 1133 15 66 16995 74778 Ex inv. 87 w HR-GA 550 1046 20 49 20920 51254 Ex inv. 88 x CR 728 1118 17 42 19006 46956 Ex inv. 89 x CR 769 1057 19 46 20083 48622 Ex inv. 90 x HR-GA 871 1071 18 44 19278 47124 Ex inv.
Table 22
Experiment Chemical ingredients Steel type Material measurement results TSxEL TSxXYS TS EL λ MPa MPa % % MPa.% MPa.% 91 Y CR 876 1233 17 46 20961 56718 Ex inv. 92 Y CR 1086 1285 16 36 20560 46260 Ex inv. 93 Y GA 896 1438 13 29 18694 41702 Ex inv. 94 Z CR 571 1029 17 50 17493 51450 Ex inv. 95 z CR 847 1159 17 37 19703 42883 Ex inv. 96 z GA 836 1103 19 51 20957 56253 Ex inv. 97 AA CR 669 1057 17 18 17969 19026 Ex comp. 98 AB CR 301 430 38 88 16340 37840 Ex comp. 99 B.C CR 679 870 12 19 10440 16530 Ex comp. 100 AD CR 630 804 17 15 13668 12060 Ex comp. 101 AE CR 700 1088 19 23 20672 25024 Ex comp. 102 AF - - - - - - - Ex comp. 103 AG CR 657 1128 15 46 16920 52315 Ex inv. 104 AG GA 682 1079 16 49 17264 53102 Ex inv. 105 AH CR 704 1163 16 43 18608 49581 Ex inv. 106 AH EG 956 1282 15 38 19230 48872 Ex inv. 107 Al CR 758 946 20 58 18920 55207 Ex inv. 108 Al Gl 632 915 18 55 16470 50450 Ex inv. 109 AJ CR 471 985 21 49 20685 48324 Ex inv. 110 AJ Gl 497 1025 19 52 19475 53166 Ex inv. 111 AK CR 597 984 20 51 19680 50125 Ex inv. 112 AK GA 564 1028 19 48 19532 49017 Ex inv. 113 AL CR 782 1075 19 38 20425 41336 Ex inv. 114 AL GA 871 1136 15 37 17040 42324 Ex inv.
[00114] Experiment 5 is an example in which the final temperature of the hot rolling mill is low. The microstructure is stretched in one direction making it irregular, so the ductility and stretch flangeability are unsatisfactory.
[00115] Experiment 10 is an example in which the cooling rate after winding is high. Cu particles precipitate
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[00116] Experiment 15 is an example in which the heating rate is high. Cu particles grow insufficiently, the ratio of Cu particles incoherent with bcc iron is small, and the stretch flangeability is unsatisfactory.
[00117] Experiment 20 is an example in which the maximum heating temperature in the annealing process is low. A large number of thick iron-based carbides that form fracture starting points are included, so ductility and stretch flangeability are unsatisfactory.
[00118] Experiment 23 is an example in which the maximum heating temperature in the annealing process is high. The Cu particles form solid solutions once during heating and there are some Cu particles that are inconsistent with bcc iron, so the stretch flangeability is unsatisfactory.
[00119] Experiment 30 is an example in which the average cooling rate of the first cooling process is high. Cu particles precipitate insufficiently, so ductility and stretch flangeability are unsatisfactory.
[00120] Experiment 34 is an example in which the average cooling rate of the first cooling process is low. Coarse iron-based carbides are formed, and stretching flangeability is unsatisfactory.
[00121] Experiment 35 is an example in which there is no tension in the first cooling process. Cu precipitation is insufficient, and stretching flangeability is unsatisfactory.
[00122] Experiment 39 is an example in which the cooling rate in the second cooling process is low. Carbides at
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54/54 thick iron bases are formed, and the stretch flangeability is unsatisfactory.
[00123] Experiment 40 is an example in which no bending is applied in the first cooling process. Cu precipitation is insufficient, and stretching flangeability is unsatisfactory.
[00124] Experiment 44 is an example in which the retention time at 250 to 500 ° C is long. Iron-based carbides form excessively, and stretching flangeability is unsatisfactory.
[00125] Experiment 45 is an example in which the retention time at 250 to 500 ° C is short. Martensite forms excessively, and the stretch flangeability is unsatisfactory.
[00126] Experiments 97 to 100 are examples in which the compositions of ingredients deviate from the predetermined range. In each case, sufficient properties could not be obtained.
[00127] Experiment 101 is an example in which the lower limit of the amount of Cu is exceeded. The density of Cu particles is low, and the stretch flangeability is unsatisfactory.

权利要求:
Claims (10)
[1]
1. High-strength steel plate, characterized by the fact that it consists of, by weight%,
C: 0.075 to 0.300%,
Si: 0.30 to 2.50%,
Mn: 1.30 to 3.50%,
P: 0.001 to 0.030%,
S: 0.0001 to 0.0100%,
Al: 0.005 to 1.500%,
Cu: 0.15 to 2.00%,
N: 0.0001 to 0.0100%, and
O: 0.0001 to 0.0100%, contains, as optional elements,
Ti: 0.005 to 0.150%,
Nb: 0.005 to 0.150%,
B: 0.0001 to 0.0100%,
Cr: 0.01 to 2.00%,
Ni: 0.01 to 2.00%,
Mo: 0.01 to 1.00%,
W: 0.01 to 1.00%,
V: 0.005 to 0.150%, and one or more of Ca, Ce, Mg, and REM: total 0.0001 to 0.50%, and a balance of iron and unavoidable impurities, in which said steel plate structure contains the ferritic phase and the martensitic phase, a ratio of Cu particles incoherent with bcc iron is 15% or more in relation to the Cu particles as a whole, a density of Cu particles in the ferritic phase is 1.0x10 ¹⁸ / m ³ or more, and an average particle size of Cu particles in the phase
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[2]
2/4 ferritic is 2.0 nm or more.
2. High strength steel plate, according to claim 1, characterized by the fact that the structure in a range of 1/8 thick to 3/8 thick of said high strength steel plate comprises, by fraction volume, a ferritic phase: 10 to 75%, ferritic-bainitic phase and / or bainitic phase: 50% or less, tempered martensitic phase: 50% or less, fresh martensitic phase: 15% or less, and residual austenitic phase: 20% or less.
[3]
3. High strength galvanized steel sheet, characterized by the fact that it comprises the high strength steel sheet, as defined in claim 1 or 2, on the surface on which a galvanized layer is formed.
[4]
4. Method of producing high-strength steel plate, characterized by the fact that it comprises a hot rolling process of heating a plate that consists of, by weight%,
C: 0.075 to 0.300%,
Si: 0.30 to 2.50%,
Mn: 1.30 to 3.50%,
P: 0.001 to 0.030%,
S: 0.0001 to 0.0100%,
Al: 0.005 to 1.500%,
Cu: 0.15 to 2.00%,
N: 0.0001 to 0.0100%,
O: 0.0001 to 0.0100%, contains, as optional elements
Ti: 0.005 to 0.150%,
Nb: 0.005 to 0.150%,
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3/4
Β: 0.0001 to 0.0100%,
Cr: 0.01 to 2.00%,
Ni: 0.01 to 2.00%,
Mo: 0.01 to 1.00%,
W: 0.01 to 1.00%,
V: 0.005 to 0.150%, and one or more of Ca, Ce, Mg, and REM: total 0.0001 to 0.50%, and a balance of iron and unavoidable impurities, directly, or after cooling once, at 1050 ° C or more, lamination with a lower temperature limit of 800 ° C or the Ar3 transformation point, whichever is greater, and winding at 500 to 700 ° C in temperature, and an annealing process to heat the steel sheet rolled by an average heating rate at 550 to 700 ° C from 1.0 to 10.0 ° C / sec. up to a maximum heating temperature of 740 to 1000 ° C, then cooling by an average cooling rate from the maximum heating temperature to 700 ° C of 1.0 to 10.0 ° C / sec, giving deformation to the plate steel from the maximum heating temperature to 700 ° C, and cooling by a cooling rate of 700 ° C to the point Bs or 500 ° C from 5.0 to 200.0 ° C / sec.
[5]
5. High-strength steel sheet production method, according to claim 4, characterized by the fact that it has a cold rolling process, after said hot rolling process and before said annealing process, of strip the rolled steel sheet, then laminate it at a tightening torque rate of 35 to 75% tightening torque.
[6]
6. High-strength steel sheet production method, according to claim 4 or 5, characterized by the fact that the deformation that is given to the steel sheet in said annealing process when applying 5 to 50 MPa of tension to the steel sheet while flexing once or more in a strip that provides a tensile strain in the outermost circumference of 0.0007 a
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4/4
0.0910,
[7]
7. Method of producing high-strength steel plate, according to claim 6, characterized by the fact that said bending is carried out by pressing the steel plate against a roller with a roller diameter of 800 mm or less.
[8]
8. High strength galvanized steel sheet production method, characterized by the fact that it produces a high strength steel sheet by the high strength steel sheet production method, as defined in any of claims 4 to 7, and then electroplates it.
[9]
9. Production method of high-strength galvanized steel sheet, characterized by the fact that it produces a high-strength steel sheet by the production method, as defined in any of claims 4 to 8, after cooling to point Bs or 500 ° C to perform hot dip galvanizing.
[10]
10. Production method of high-strength galvanized steel sheet, according to claim 9, characterized by the fact that it performs the bonding treatment at 470 to 650 ° C in temperature after hot dip galvanizing.

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法律状态:
2018-08-07| B06A| Notification to applicant to reply to the report for non-patentability or inadequacy of the application according art. 36 industrial patent law|

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2018-12-11| B09A| Decision: intention to grant|

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2019-01-08| B16A| Patent or certificate of addition of invention granted|Free format text: PRAZO DE VALIDADE: 20 (VINTE) ANOS CONTADOS A PARTIR DE 27/07/2012, OBSERVADAS AS CONDICOES LEGAIS. |

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2019-11-19| B25D| Requested change of name of applicant approved|Owner name: NIPPON STEEL CORPORATION (JP) |

优先权:

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申请号 | 申请日 | 专利标题

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JP2011167816|2011-07-29|

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PCT/JP2012/069226|WO2013018723A1|2011-07-29|2012-07-27|High-strength zinc-plated steel sheet and high-strength steel sheet having superior moldability, and method for producing each|

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