hot stamped part and production method

专利摘要:
the present invention relates to a hot stamped part having a chemical composition represented, in mass%, by: c: 0.120% to 0.400%; si: 0.005% to 2,000%; mn or cr, or both: 1.00% to 3.00% in total; al: 0.005% to 0.100%; b: 0.0003% to 0.0020%; p: no more than 0.030%; s: no more than 0.0100%; o: no more than 0.0070%; n: not more than 0.0070%; ti: 0% to 0.100%; nb: 0% to 0.100%; v: 0% to 0.100%; ni: 0% to 2.00%; cu: 0% to 2.00%; mo: 0% to 0.50%; ca or rem, or both: 0% to 0.0300% in total; and the balance: faith and impurities. hot stamped part has a structure represented by: a fraction of area of martensite or bainite, or both: not less than 95% in total; a grain cover factor of the previous austenite by iron-based carbides: no more than 80%; and a numerical density of the iron-based carbides in the grains of the previous austenite: not less than 45 / ¿m2.
公开号:BR112015032803B1
申请号:R112015032803
申请日:2014-09-12
公开日:2020-01-14
发明作者:Abukawa Genki；Kawasaki Kaoru；Azuma Masafumi
申请人:Nippon Steel & Sumitomo Metal Corp；Nippon Steel Corp；
IPC主号:

专利说明:

Descriptive Report of the Invention Patent for HOT STAMPED PIECE AND THE SAME PRODUCTION METHOD.
Technical field [001] The present invention relates to a hot stamped part used for an automobile chassis or others, and to a method of producing the hot stamped part.
Background [002] In recent years, the weight reduction of an automobile chassis has been a crucial point from the point of view of protecting global environments, and studies on the application of a high-strength steel sheet to a chassis part vehicles have been actively driven. As the strength of the used steel plate has increased even more, considerations about its working capacity and the capacity to fix the shape have become important. In addition, since the forming load in the press forming increases as the strength of the steel plate increases, increasing the pressing capacity has also been one of the main points.
[003] Forming by hot stamping (hereinafter also referred to simply as hot stamping) is a technique in which a steel sheet is heated to a high temperature in a strip of austenite and subjected to forming by pressing while it is high temperature. Once a softened steel sheet is formed in hot stamping, more complicated jobs can be performed. In addition, in hot stamping, as the rapid cooling is performed at the same time as the press forming to make the steel sheet structure undergo the transformation of martensite, it is possible to achieve strength and ability to
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2/56 fixing the shape according to the carbon content of the steel sheet at the same time. In addition, since the softened steel sheet is subjected to forming in the hot stamping forming, it is possible to significantly reduce the forming load compared to the common pressing forming that is carried out at room temperature.
[004] A hot stamped part, which is produced by forming by hot stamping, especially a hot stamped part for an automobile chassis requires excellent low temperature toughness. A hot stamped part is sometimes called a sheet steel element. Techniques relating to increases in toughness and ductility are described in Patent References 1 to 5. However, the techniques described in Patent References 1 to 5 cannot provide sufficient toughness at low temperature. Although Patent References 6 to 10 also describe techniques relating to hot press forming or the like, they also cannot provide sufficient toughness at low temperature.
List of citations
Patent References [005] Patent Reference 1: Japanese Patent Publication
Open to Public Inspection No. 2006-152427 [006] Patent Reference 2: Japanese Patent Publication
Open to Public Inspection No. 2012-180594 [007] Patent Reference 3: Japanese Patent Publication
Open to Public Inspection No. 2010-275612 [008] Patent Reference 4: Japanese Patent Publication
Open to Public Inspection No. 2011-184758 [009] Patent Reference 5: Japanese Patent Publication
Open to Public Inspection No. 2008-264836
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3/56 [0010] Patent Reference 6: Japanese Patent Publication
Open to Public Inspection No. 2001-161481 [0011] Patent Reference 7: Japanese Patent Publication
Open to Public Inspection No. 07-18322 [0012] Patent Reference 8: International Publication Pamphlet No. WO 2012/169640 [0013] Patent Reference 9: Japanese Patent Publication
Open to Public Inspection No. 2013-14842 [0014] Patent Reference 10: Japanese Patent Publication
Open to Public Inspection No. 2005-205477
Summary of the invention
Technical problem [0015] It is an objective of the present invention to provide a hot stamped part that can achieve excellent tensile strength and low temperature toughness, and a method of producing it.
Solution to the problem [0016] The present inventors conducted intense studies on the causes of the difficulty in achieving sufficient toughness at low temperature for a conventional hot stamped part. As a result, it has been found that iron-based carbides precipitate near all the contours of the previous austenite grains and an intergranular fracture is more likely to occur. The present inventors have also discovered that the cooling rate during hot stamping is an important factor in inhibiting the precipitation of iron-based carbides in the contours of the previous austenite grains.
[0017] Consequently, based on these findings, the present inventors came to conceive various aspects of the invention described below.
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4/56 [0018] (1) A hot stamped part, including:
[0019] a chemical composition represented, in% by mass, by [0020] C: 0.120% to 0.400%;
[0021] Si: 0.005% to 2,000%;
[0022] Mn or Cr, or both: 1.00% to 3.00% in total;
[0023] Al: 0.005% to 0.100%;
[0024] B: 0.0003% to 0.0020%;
[0025] P: no more than 0.030%;
[0026] S: no more than 0.100%;
[0027] O: no more than 0.0070%;
[0028] N: not more than 0.0070%;
[0029] Ti: 0% to 0.100%;
[0030] Nb: 0% to 0.100%;
[0031] V: 0% to 0.100%;
[0032] Ni: 0% to 2.00%;
[0033] Cu: 0% to 2.00% [0034] Mo: 0% to 0.50%;
[0035] Ca or REM, or both: 0% to 0.0300% in total; and [0036] the balance: Fe and impurities; and [0037] a structure represented by:
[0038] a fraction of the area of martensite or bainite, or both:
not less than 95% in total;
[0039] a covering factor of the grain contour of the previous austenite by carbides based on iron: no more than 80%; and [0040] the numerical density of the iron-based carbides in the grains of the previous austenite: not less than 45 / pm ² .
[0041] (2) The hot stamped part according to item (1), where the chemical composition satisfies:
[0042] Ti: 0.005% to 0.100%;
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5/56 [0043] Nb: 0.005% to 0.100%; or [0044] V: 0.005% to 0.100%; or [0045] any of its combinations.
[0046] (3) The hot stamped part according to item (1) or (2), where the chemical composition satisfies:
[0047] Ni: 0.05% to 2.00%;
[0048] Cu: 0.05% to 2.00%; or [0049] Mo: 0.05% to 0.50%; or [0050] any of its combinations.
[0051] (4) The hot stamped part according to item (1) to (3), where the chemical composition satisfies:
[0052] Ca or REM, or both: 0.0005% to 0.0300% in total.
[0053] (5) A method of producing a hot stamped part, including the steps of:
[0054] heat a steel plate to a temperature of not less than the point Ac3 and not more than 950 ° C at an average heating rate of not less than 2 ° C / s;
[0055] then cool the steel sheet over a temperature range from point Ar3 to (point Ms - 50) ° C at an average cooling rate of not less than 100 ° C / s while performing the hot pressing ; and [0056] then, cool the steel sheet over a temperature range from (point Ms - 50) ° C to 100 ° C at an average cooling rate of no more than 50 ° C / s, [0057] where [0058] the steel plate includes a chemical composition represented, in mass%, by:
[0059] C: 0.120% to 0.400%;
[0060] Si: 0.005% to 2,000%;
[0061] Mn or Cr, or both: 1.00% to 3.00% in total;
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6/56 [0062] Al: 0.005% to 0.100%;
[0063] B: 0.0003% to 0.0020%;
[0064] P: no more than 0.030%;
[0065] S: no more than 0.0100%;
[0066] O: no more than 0.0070%;
[0067] N: not more than 0.0070%;
[0068] Ti: 0% to 0.100%;
[0069] Nb: 0% to 0.100%;
[0070] V: 0% to 0.100%;
[0071] Ni: 0% to 2.00%;
[0072] Cu: 0% to 2.00%;
[0073] Mo: 0% to 0.50%;
[0074] Ca or REM, or both: 0% to 0.0300% in total; and [0075] the balance: Fe and impurities, and [0076] the maximum cooling rate is no more than 70 ° C / s and the minimum cooling rate is no less than 5 ° C / s over a temperature range of (Ms - 120 point) ° C to 100 ° C.
[0077] (6) The production method of the hot stamped part according to item (5), where the chemical composition satisfies:
[0078] Ti: 0.005% 0 to 100%;
[0079] Nb: 0.005% to 0.100%; or [0080] V: 0.005% to 0.100%; or [0081] any of its combinations.
[0082] (7) The production method of the hot stamped part according to item (5) or (6), where the chemical composition satisfies:
[0083] Ni: 0.05% to 2.00%;
[0084] Cu: 0.05% to 2.00%; or [0085] Mo: 0.05% to 0.50%; or [0086] any of its combinations.
[0087] (8) The method of producing the hot stamped part
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7/56 according to any of items (5) to (7), where the chemical composition satisfies:
[0088] Ca or REM or both: 0.0005% to 0.0300% in total.
Advantageous effects of the invention [0089] According to the present invention, it is possible to achieve excellent tensile strength and low temperature toughness. Brief description of the drawings [0090] [Figure 1] - Figure 1 is a schematic diagram illustrating an anterior austenite grain, and iron-based carbides that have precipitated around the grain boundary.
Description of modalities [0091] Hereinafter, modalities of the present invention will be described. A hot stamped part according to one embodiment of the present invention is produced, as described in greater detail below, by forming by hot stamping including the rapid cooling of a steel sheet for hot stamping. Thus, the hardening capacity and rapid cooling conditions of the hot stamping steel sheet affect the hot stamped part.
[0092] In the beginning, a structure of a hot stamped piece will be described according to the present modality. The hot stamped part according to the present modality includes a structure represented by: A fraction of area of martensite or bainite, or both: not less than 95% in total; a covering factor of the grain contour of the previous austenite by the iron-based carbides: no more than 80%, and the numerical density of the iron-based carbides in the grains of the previous austenite: no less than 45 / pm ² .
[0093] A fraction of the area of martensite or bainite, or both:
not less than 95% in total [0094] Martensite and bainite, particularly martensite, are imposed
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8/56 to achieve the strength of a hot stamped part. If the total area fraction of martensite and the area fraction of bainite is less than 955, it is not possible to achieve sufficient strength, for example, a tensile strength of not less than 1180 MPa. Therefore, the area fraction of martensite and the area fraction of bainite are no less than 95% in total. The martensite can be, for example, either initial martensite or tempered martensite. The tempered martensite obtained in the present embodiment is, for example, self-tempered martensite. Initial martensite is martensite as it cools quickly. Tempered martensite includes iron-based carbides that precipitate after or during quench cooling. Tempered martensite includes iron-based carbides that precipitate after or during quench cooling. Self-tempered martensite is tempered martensite which is generated during cooling in rapid cooling without being subjected to heat treatment for tempering. To achieve the desired strength with more certainty, the fraction of area of martensite is preferably greater than the fraction of area of bainite, and the fraction of area of martensite is preferably not less than 70%.
[0095] The balance different from martensite and bainite is one or more between ferrite, perlite or austenite retained, for example. Their quantities are preferably as low as possible.
[0096] The identification of martensite, bainite, ferrite, perlite and retained austenite, the confirmation of their positions, and the measurement of their area fractions can be performed by observing the cross section parallel to the rolling direction and the thickness direction , or a cross section orthogonal to the rolling direction of a hot stamped part. The observation of a cross section can be performed, for example, by etching the cross section of a Nital reagent, and observing it at a magnification of 1000 to 100000 times with a scanning electron microscope (SEM) or
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9/56 an electronic transmission microscope (TEM). Other caustication solutions can be used in place of the Nital reagent. An example of a caustic solution that can be used is described in Japanese Patent Publication Open to Public Inspection No. 59219473. The caustic solution described in Japanese Patent Publication Open to Public Inspection No. 59-219473 is a colored caustic solution characterized by consisting of a pre-treatment solution and a post-treatment solution, in which the pre-treatment solution is prepared by mixing solution A in which 1 to 5 g of picric acid is dissolved in 100 ml of ethanol , with a solution B in which 1 to 25 g of sodium thiosulfate and 1 to 5 g of citric acid are dissolved in 100 ml of water, in a ratio of 1: 1, and later adding 1.5 to 4% of nitric acid to the solution, and the post-treatment solution is prepared by mixing 10% of the pretreatment solution with a 2% Nital solution, or by mixing 2 to 5% nitric acid with 100 ml of ethanol . The analysis of the crystal orientation using a field emission scanning electron microscope (FE-SEM) can also be performed to identify structures, confirm their positions, and measure their area fraction. Structures can also be determined by measuring the hardness of a minimum region, such as measuring micro Vickers hardness.
[0097] The fractions of area of bainite and martensite can also be measured as follows. For example, a sample is obtained that has a cross section parallel to the rolling direction and the thickness direction of a steel sheet as an observation surface, the observation surface is electropolished, and a portion of the steel sheet at a depth 1/8 to 3/8 of its thickness from the surface is observed with an FE-SEM. On that occasion, each measurement is performed at a magnification of 5000 times in 10 visual fields, the fraction of area is assumed to be its average value. The martensi
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10/56 observed may also include tempered martensite. Since the martensite may not be sufficiently etched by the Nital reagent, the ferrite and bainite area fractions can be measured by the method described above using an FE-SEM, and the martensite area fraction can be considered to be the fraction of area of the non-rustic portion that is observed by FE-SEM. The area fraction of the retained austenite can also be determined from measuring the intensity by X-ray diffraction. For example, it can be determined from an X-ray diffraction intensity ratio between ferrite and austenite. Ferrite, which is made of coarse grains, means a structure that does not include any substructure such as an internal slat.
[0098] Factor covering the grain contour of the previous austenite by carbides based on iron: no more than 80% [0099] Factor covering the grain contour of the austenite anterior by carbides based on iron means the ratio of the portions in which iron-based carbides have precipitated within the grain outline of the previous austenite. The grain contour portions of the previous austenite where iron-based carbides have precipitated appear to be covered with iron-based carbides when viewed under a microscope. If the ratio of the portions in which the iron-based carbides precipitated within the austenite grain contour above is greater than 80%, the intergranular fracture is more likely to occur, and therefore a sufficient low temperature toughness cannot be achieved . Therefore, the coverage factor is no more than 80%. To also achieve excellent toughness at low temperature, the coverage factor is preferably no more than 70%, more preferably no more than 60%.
[00100] Numerical density of iron-based carbides in grains from the previous austenite: not less than 45 / pm ² [00101] Iron-based carbides in the grains of the previous austenite
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11/56 contribute to the increase in toughness at low temperature. If the numerical density of the iron-based carbides in the grains of the previous austenite is less than 45 / pm ² , it is not possible to achieve a toughness at sufficient low temperature. Therefore, the numerical density is no less than 45 / pm ² . In order to achieve a more excellent low temperature toughness, the numerical density is preferably not less than 50 / pm ² . If the numerical density is greater than 200 / pm ² , the effect of increasing toughness at low temperature is saturated. Therefore, the numerical density is preferably not more than 200 / pm ² .
[00102] An iron-based carbide is a compound consisting of iron and carbon, examples of which include cementite (Θ phase), ε phase, and χ phase. As described below, Si or the like can be dissolved in and contained in iron carbide. Non-iron-containing carbides, such as Ti carbides and Nb carbides do not correspond to iron-based carbide.
[00103] Here, a method of determining the grain contour coverage factor of the anterior austenite by iron carbides will be described in relation to Figure 1. Figure 1 is a schematic diagram illustrating an anterior austenite grain, and carbides based of iron that precipitated in the grain outline.
[00104] In the example illustrated in Figure 1, a front austenite grain 21 that has a hexagonal shape on an observation surface is included in a hot stamped part. Iron-based carbides 1 and 2 precipitate on a first side 31, iron-based carbides 3 and 4 precipitate on a second side 32, iron-based carbides 5, 6 and 7 precipitate on a third side 33, a carbide at iron base 8 precipitates on a fourth side 34, iron based carbides 9 and 10 precipitate on a fifth side 35, and iron base carbides 11 and 12 precipitate on a sixth side 36. The length of the side
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12/56 is Li, the length of side 32 is L2, the length of side 33 is L3, the length of side 34 is L4, the length of side 35 is L5, and the length of side 36 is L6. The lengths of the iron-based carbides 1 and 2 in the grain boundaries are Xi and X2, respectively; the lengths of the iron-based carbides 3 and 4 in the grain boundaries are X3 and X4, respectively; the lengths of the iron-based carbides 5, 6 and 7 in the grain boundaries are X5, X6 and X7 respectively; the length of the iron-based carbide 8 in the grain boundaries is X8; the lengths of the iron-based carbides 9 and 10 in the grain boundaries are X9 and X10, respectively; the lengths of the iron-based carbides 11 and 12 in the grain boundaries are X11 and X12, respectively. Note that the length of an iron-based carbide in the grain outline means the distance between two points of intersection between an iron-based carbide and the grain outline on an observation surface.
[00105] Then, the sum L (pm) of the lengths of the six sides 31 to 36 is discovered, and the sum X (pm) of the lengths of the iron-based carbides 1 to 12 in the grain boundary is discovered to determine a value represented by (X / L x 100 (%) as a coverage factor. Note that when determining the coverage factor in a hot stamped part, the coverage factors are determined for every 10 or more previous austenite grains included in the hot stamped part, and its average value is assumed to be the covering factor in the hot stamped part.The contour of the previous austenite grain is considered to be the part that is made to appear by a caustic solution containing sodium dodecylbenzenesulfonate, and a anterior austenite grain and iron-based carbides precipitated in their grain boundaries are observed with an FE-SEM.
[00106] Although the former austenite grain 21 which has a hexagonal shape on an observation surface is illustrated as a
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13/56 example in Figure 1, in general, the actual anterior austenite grains have more complex shapes. Therefore, in practice, sides of an anterior austenite grain are identified according to the shape of the observed austenite grain observed, and the sum of the lengths of each side is determined. When a curved portion is present in a grain boundary, the portion can be approximated to a plurality of sides.
[00107] Subsequently, the chemical composition of a hot stamped part according to a modality of the present invention and a steel plate used to produce the hot stamped part will be described. In the following description, the% symbol, which is the unit of each element contained in a hot stamped part and on the steel plate used to produce the hot stamped part, means, unless otherwise specified, mass% . A hot stamped part and a steel plate used to produce the hot stamped part have a chemical composition represented by: C: 0.120% to 0.400%; Si: 0.005% to 2,000%; Mn or Cr, or both: 1.00% to 3.00% in total; Al: 0.005% to 0.100%; B: 0.0003% to 0.0020%; P: no more than 0.030%; S: not more than 0.0100%; O: not more than 0.0070%; N: not more than 0.0070%; Ti: 0% to 0.100%; Nb: 0% to 0.100%; V: 0% to 0.100%; Ni: 0% to 2.00%; Cu: 0% to 2.00%; Mo: 0% to 0.50%; Ca or REM (rare earth metal), or both: 0% to 0.0300% in total; and the balance: Fe and impurities. As impurities, those contained in raw materials such as ores and scrap are exemplified, and those introduced in the production process.
[00108] C: 0.120% to 0.400% [00109] C (carbon) is an element to increase the resistance of a hot stamped part. When the C content is less than 0.120%, the effect by the function described above cannot be achieved sufficiently. For example, it is not possible to obtain resistance to
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14/56 traction of not less than 1180 Mpa. Therefore, the C content is not less than 0.120%. To obtain more excellent strength, the C content is preferably not less than 0.140%, and more preferably not less than 0.150%. When the C content is greater than 0.400%, the resistance is excessive, and a sufficient low temperature toughness cannot be achieved. In addition, it is also difficult to achieve sufficient welding capacity and working capacity. Therefore, the C content is no more than 0.400%. To obtain a more excellent low temperature toughness, the C content is preferably not more than 0.370%, but more preferably not more than 0.350%.
[00110] Si: 0.005% to 2,000% [00111] Si (Silicon) is an element that dissolves in an iron-based oxide thus increasing resistance to hydrogen embrittlement. Although a detailed correlation between Si and resistance to embrittlement by hydrogen is not clear, it is deduced that the elastic tension at the interface between the iron-based carbide and the matrix phase increases as a result of the dissolution of Si in the iron-based carbide, and thus the ability to capture hydrogen from the iron-based carbide is increased. When the Si content is less than
0.005%, the effect of the function described above cannot be achieved sufficiently. Therefore, the Si content is not less than 0.005%. In order to obtain a more excellent hydrogen embrittlement resistance, the Si content is preferably not less than 0.01%, and more preferably not less than 0.15%. When the Si content is greater than 2,000%, the effect of increasing resistance to hydrogen embrittlement is saturated, and the Ac3 point is excessively high, thus unjustly increasing the heating temperature in the hot stamping conformation. Therefore, the Si content is no more than 2,000%. Considering the balance between resistance to embrittlement
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15/56 by hydrogen and the Acs point, the Si content is preferably no more than 1,600%.
[00112] Si also affects the coating capacity and the delayed fracture characteristic. For example, when the Si content is greater than 0.005%, the coating capacity deteriorates, thus sometimes resulting in flaking or coating. For this reason, when a coated steel sheet is used as a hot stamping steel sheet, the Si content is preferably no more than 0.500%. On the other hand, Si increases the characteristic of delayed fracture. Therefore, when a coated steel sheet is used as a hot stamping steel sheet, the Si content is preferably not less than 0.500% to achieve excellent resistance to delayed fracture.
[00113] Mn or Cr, or both: 1.00% to 3.00% in total [00114] Mn (manganese) and Cr (chromium) are important elements to delay the transformation of ferrite during cooling when forming by hot, and thus obtaining the desired structure of a hot stamped part to be described below. When the total content of Mn and Cr content is less than 1.00%, it is possible that ferrite and perlite are formed during cooling in hot stamping, and the desired structure cannot be obtained. Thus, once the desired structure has not been obtained, it is not possible to achieve sufficient strength, for example, a tensile strength of not less than 1180 Mpa. Therefore, the total content of Mn and Cr content is not less than 1.00%. To achieve more excellent strength, the total Mn and Cr content is preferably not less than 1.30%, and more preferably not less than 1.40%. When the total content of Mn and Cr content is greater than 3.00%, the effect of delaying the transformation of ferrite and thus increasing the resistance is saturated. In addition, the resistance of
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16/56 hot rolled steel sheet increases excessively, and thus sometimes the break occurs during cold rolling, and / or the wear and tear of the blade to be used for cutting is sometimes pronounced. Therefore, the total content of Mn and Cr content is no more than 3.00%. Considering an adequate resistance range, the total content of Mn and Cr is preferably not more than 2.9%, and more preferably not more than 2.8%. When Mn is excessively contained, embrittlement occurs due to the segregation of Mn, and thus a problem such as breakage of the cast plate is more likely to occur, and also the weldability is likely to deteriorate. Although the content of each element between Mn and Cr is no less than 0.8%, and the Cr content is no less than 0.2%, for example. [00115] Al: 0.005% to 0.100% [00116] Al (aluminum) is an effective element for deoxidation. When the Al content is less than 0.005%, deoxidation is insufficient, and a large amount of oxides can remain in a hot stamped part, particularly deteriorating the local deformation capacity. In addition, variations in characteristics increase. Therefore, the Al content is not less than 0.005%. For sufficient deoxidation, the Al content is preferably not less than 0.006%, and more preferably not less than 0.007%. When the Al content is greater than 0.100%, a large amount of oxides consisting mainly of alumina remains in a hot stamped part, thus deteriorating the deformation capacity. Therefore, the Al content is not more than 0.100%. To suppress the remaining alumina, the Al content is preferably not more than 0.08%, and more preferably not more than 0.075%.
[00117] B: 0.0003% to 0.0020% [00118] B (boron) is an element to increase the hardening capacity of a steel sheet for hot stamping.
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17/56
As a result of the increased hardening capacity, it is easier to obtain martensite in the structure of the hot stamped part. When the B content is less than 0.0003%, the effect by the function described above has not been sufficiently achieved. To achieve a more excellent curing capacity, the B content is preferably not less than 0.0004%, and more preferably not less than 0.0005%. When the B content is greater than 0.0020%, the effect of increasing the hardening capacity is saturated, and iron-based borides precipitate, thus deteriorating the hardening capacity. Therefore, the B content is no more than 0.0020%. To suppress the precipitation of the iron-based borides, the B content is preferably not more than 0.0017%.
[00119] P: no more than 0.030% [00120] P (phosphorus) is not an essential element, and is contained in steel as an impurity, for example. P is an element that secretes in an intermediate portion in the direction of the thickness of the steel plate, thus weakening the welded area. For this reason, the P content is preferably as low as possible. Particularly, when the P content is greater than 0.030%, the embrittlement of the welded zone is pronounced. Therefore, the P content is no more than 0.030%. The P content is preferably not more than 0.020%, and more preferably not more than 0.015%. Reducing the P content is expensive, and reducing it to less than 0.001% increases the cost noticeably. For this reason, the P content can be no less than 0.001%.
[00121] S: no more than 0.0100% [00122] S (sulfur) is not an essential element and is contained in steel as an impurity, for example. S is an element that hinders the casting and hot rolling in the production of a steel sheet, thus deteriorating the welding capacity of a hot stamped part. For this reason, the S content is preferably as
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18/56 as low as possible. Particularly, when the S content is greater than 0.0100%, the adverse effects are pronounced. Therefore, the S content is not more than 0.0100%. The S content is preferably not more than 0.008%, and more preferably not more than 0.005%. Reducing the S content is expensive, and reducing it by less than 0.0001% increases the cost noticeably. For this reason, the S content should be no less than 0.0001%.
[00123] O: no more than 0.0070% [00124] O (oxygen) is not an essential element and is contained in steel as an impurity, for example. O is an element that forms oxides, and thus causes the deterioration of the properties of a steel sheet for hot stamping. For example, oxides that are in the vicinity of the steel sheet surface can cause a surface failure, thereby deteriorating the appearance quality. If an oxide is on a cut surface, it forms a notch in the cut surface, causing the properties of a hot stamped part to deteriorate. For this reason, the O content is preferably as low as possible. Particularly, when the O content is greater than 0.0070%, the deterioration of properties is pronounced. Therefore, the O content is no more than 0.0070%. The O content is preferably not more than 0.0050%, and even more preferably not more than 0.0040%. Reducing the O content is expensive, and reducing it to less than 0.0001% increases the cost noticeably. For this reason, the O content can be no less than 0.0001%.
[00125] N: no more than 0.0070% [00126] N (nitrogen) is not an essential element, and is contained in steel as an impurity, for example. N is an element that forms crude nitrides, thus deteriorating the folding capacity and the hole expansion capacity. N also causes bubbles to occur during welding. For this reason, the N content is preferable
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19/56 as low as possible. Particularly, when the N content is greater than 0.0070%, the deterioration of the folding capacity and the expansion capacity of the hole is pronounced. Therefore, the N content is not more than 0.0070%. Reducing the N content is expensive, and reducing it to less than 0.0005% increases the cost noticeably. For this reason, the N content should be no less than 0.0005%. In addition, from the point of view of production cost, the N content must be not less than 0.0010%.
[00127] Ti, Nb, V, Ni, Cu, Mo, Ca, and REM are not essential elements, and are optional elements that can be adequately contained in a predetermined quantity as a limit on a steel plate for hot stamping, and in a hot stamped piece.
[00128] Ti: 0% to 0.100%, Nb: 0% to 0.100%, V: 0% to 0.100% [00129] Ti, Nb, and V are elements that inhibit the growth of the crystal grain of the austenite phase during conformation by hot stamping and thus contribute to increase the strength and toughness by reinforcing the grain refining of the transformed structure. Ti also has the function of combining with N to form TiN, thus inhibiting the formation of nitride by B. Therefore, one or any combination selected from the group consisting of these elements may be contained. However, when anyone between the Ti content, the Nb content and the V content is greater than 0.100%, Ti carbides, Nb carbides, or V carbides are formed excessively, resulting in a deficiency in the amount of C, which contributes to the strengthening of the martensite, so that sufficient strength cannot be achieved. Therefore, all of the Ti content, the Nb content and the V content are no more than 0.100%. Anything between the Ti content, the Nb content, and the V content is preferably not more than 0.080%, and more preferably not more than 0.050%. To achieve with certainty
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The effect of the function described above, all between the Ti content, the Nb content, and the V content are preferably not less than 0.005%. That is, it is preferable that Ti: 0.005% to 0.100%, Nb: 0.005% to 0.100%, or V: 0.005% to 0.100%, or any of its combinations is satisfied. [00130] Ni: 0% to 2.00%, Cu: 0% to 2.00%, Mo: 0% to 0.50% [00131] Ni, Cu, and Mo are elements that increase the hardening capacity of a steel plate for hot stamping. As a result of the increased hardening capacity, it is more likely that martensite is formed in the structure of a hot stamped part. Therefore, one or any combination selected from the group consisting of these elements may be contained. However, when either the Ni content or the Cu content is greater than 2.00%, or the Mo content is greater than 0.50%, the welding capacity and the hot-working capacity deteriorate. Therefore, both the Ni and Cu contents are no more than 2.00%, and the Mo content is no more than 0.50%. To achieve with certainty the effect of the function described above, any one between the Ti content, the Cu content, and the Mo content is preferably not less than 0.01%. That is, it is preferable that Ni: 0.05% to 2.00%, Cu: 0.05% to 2.00%, or Mo: 0.05% to 0.50%, or any of its combinations are satisfied .
[00132] Ca or REM, or both: 0% to 0.0300% in total [00133] Ca and REM are elements that contribute to increase strength, and to improve toughness through the structure. Therefore, Ca or REM or both can be contained. However, when the total Ca content and REM content are greater than 0.0300%, the casting capacity and the hot working capacity deteriorate. Therefore, the total Ca content and REM content are no more than 0.0300%. To achieve the effect of the function described above with certainty, the total Ca content and REM content are preferably not less than 0.0005%. That is, it is preferable that Ca or REM, or both:
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21/56
0.0005% to 0.0300% in total is satisfied. REM de refers to elements belonging to Sc, Y, and elements belonging to the series of lantanoids, and the REM content means the total content of these elements. Industrially, REM is often added as a metal misch, and contains multiple types of elements such as La and Ce. A metallic element belonging to the REM, such as La metallic and Ce metallic, can be added alone.
[00134] According to a hot stamped part in accordance with the present modality, it is possible to achieve excellent tensile strength and tenacity at low temperature since it has adequate chemical composition and structure.
[00135] Subsequently, a method of producing the hot stamped part will be described according to the mode of the present invention. According to the method described here, it is possible to produce the hot stamped part according to the embodiment of the present invention.
[00136] In the production method, a steel sheet for hot stamping, which has the chemical composition described above, is heated to a temperature of not less than the point Ac3 and not more than 950 ° C at an average rate of heating not less than 2 ° C / s; it is then cooled over a temperature range from point Ar3 to (point Ms - 50) ° C at an average cooling rate of not less than 100 ° C / s while performing the hot pressing; and it is also cooled over the temperature range (point Ms 50) ° C to 100 ° C at an average cooling rate of no more than 50 ° C / s. The maximum cooling rate is not more than 70 ° C / s, and the minimum cooling rate is no less than 5 ° C / s in the temperature range (point Ms - 120) ° C to 100 ° C.
[00137] Heating temperature: not less than Ac3 and not more than 950 ° C
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22/56 [00138] The temperature to which the steel sheet for hot stamping is heated is not less than point AC3 and not more than 950 ° C. The steel sheet is made to have a single-phase austenite structure by heating the steel sheet to a temperature of not less than the point Ac3. It is possible to obtain a structure in which the area fraction of the martensite and the area fraction of the bainite are not less than 95%, thus obtaining a high strength, for example, a tensile strength of not less than 1180 MPa by subjecting to steel plate having a single phase austenite structure for rapid cooling. Since the structure of the steel plate includes ferrite when the heating temperature mentors that point Ac3, even if such rapid cooling of the steel plate is carried out, the ferrite grows and it is not possible to obtain a tensile strength of no less than 1180 MPa. Therefore, the heating temperature is no less than the point Ac3. When the heating temperature is greater than 950 ° C, the austenite grains become crude, and the low temperature toughness after rapid cooling deteriorates. Therefore, the heating temperature is no more than 950 ° C.
[00139] The point Ac3 can be determined using the following formula:
[00140] point Ac3 (° C) = 910 - 203 / C - 30Mn - 11Cr + 44.7Si + 400Al + 700P - 15.2Ni - 20Cu + 400Ti + 104V + 31.5Mo [00141] (C, Mn, Cr , Si, Al, P, Ni, Cu, Ti, V, and Mo each represent a content (% by mass) of each component in the steel plate).
[00142] If Ni, Cu, Ti, V and / or Mo, which are optional elements, are not contained in the steel sheet, the content of each element that is not contained is supposed to be 0 (mass%).
[00143] Average heating rate: not less than 2 ° C / s [00144] When the average heating rate is less than 2 ° C / s, the austenite grains become crude during heating, and the temperature
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23/56 nance at low enough temperature and delayed fracture resistance cannot be achieved. Therefore, the average rate of heating during heating to a temperature of not less than the point Ac3 and not more than 950 ° C is not less than 2 ° C / s. In order to also inhibit the bruising of the austenite grains, the average heating rate is preferably not less than 3 ° C / s, and more preferably not less than 4 ° C / s. In addition, increasing the heating rate is also effective in increasing productivity. The effects of the modality of the present invention can be achieved even without particularly adjusting an upper limit on the average rate of heating. Therefore, the average heating rate can be adjusted accordingly taking into account the capacity of the production facility as well as the heating equipment, without particularly adjusting the upper limit of the average heating rate. Here the average heating rate is the value obtained by dividing the difference between the temperature at which heating is started and the heating temperature for a period of time taken for heating.
[00145] After being heated to a temperature of not less than the point Ac3 and not more than 950 ° C at an average heating rate of not less than 2 ° C / s, the steel sheet is cooled while being subjected to pressing the hot. That is, forming by hot stamping is carried out. The transformation and precipitation of iron-based carbides occurs according to the temperature during cooling. Here, the relationship between temperature, and transformation and precipitation of iron-based carbides will be described.
[00146] In the beginning, in the temperature range from the heating temperature to the Ar3 point, a transformation such as the transformation of ferrite, and the precipitation of the iron-based carbides does not occur. Therefore, the cooling rate in this temperature range does not affect the structure of a hot stamped part. Once
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24/56 the temperature of the steel plate reaches the point Ar3, the transformation of ferrite and / or the transformation of perlite can start depending on the cooling rate, and also since the temperature falls within a temperature range lower than the point A1, iron-based carbides begin to precipitate. Therefore, the cooling rate in the temperature range of no more than the Ar3 point significantly affects the structure of the hot stamped part. Iron-based carbides precipitate both in the grain contour and in the grain of the previous austenite, and they are more likely to precipitate in the grain contours at a temperature of not less than (point Ms - 50) ° C, and in a grain at a temperature of more than (point Ms 50) ° C. Therefore, it is important to change the average cooling rate to a temperature of (Ms - 50 point) ° C. The precipitation of iron-based oxides is very unlikely to occur at a temperature of less than 100 ° C, and the transformation does not occur at less than 100 ° C. Therefore, the cooling rate in this temperature range also does not affect the structure of a hot stamped part. Then, in the present mode, the cooling rate in a temperature range from point Ar3 to (point Ms - 50) ° C, and the cooling rate in a temperature range from (point Ms - 50) ° C to 100 ° C is specified.
[00147] The Ar3 point (transformation point Ar3) and the point Ms can be discovered using the following formulas:
[00148] point Ar3 (° C) = 901 - 325C + 33Si - 92 (Mn + Ni / 2 + Cr / 2 + Cu / 2 + Mo / 2) [00149] point Ms (° C) = 561 - 474C - 33Mn - 17Ni - 17Cr - 21Mo [00150] (C, Si, Mn, Ni, Cr, Cu, and Mo each represent the content (% by mass) of each component in the steel plate).
[00151] If Ni, Cu, Ti, V and / or Mo, which are optional elements, are not contained in the steel plate, the content of any element that
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25/56 is not contained it is supposed to be 0 (mass%).
[00152] Since there is a correlation as described above between temperature, and transformation and precipitation of iron-based carbides, it is conceived that the cooling rate is controlled for each of the following four temperature ranges. The four temperature ranges include a first temperature range from the heating temperature to point Ar3, a second temperature range from point Ar3 to (point Ms - 50) ° C, a third temperature range from (point Ms - 50) ° C to 100 ° C, and a fourth temperature range of less than 100 ° C.
First temperature range [00153] In the first temperature range (from the heating temperature to the point Ar3), since neither the transformation, such as the transformation of ferrite, as described above, nor precipitation of carbides based occur, there is no need to control the cooling speed especially. However, considering that the average cooling rate in the second temperature range is not less than 100 ^o C / s, as described below, it is preferable that the average cooling rate in the first temperature range is not less than 100 ^o C / s.
Second temperature range [00154] In the second temperature range (from point Ar3 to (point Ms - 50) ° C), the transformation of ferrite and the transformation of perlite occur depending on the cooling rate, as well as the carbides based iron precipitate in the temperature range below point A1, as described above. If the average cooling rate in the second temperature range is not less than 100 ° C / s, it is possible to avoid the transformation of ferrite and the transformation of perlite, thus making the total fraction of the martensite area and the fraction of the area of bainite be no less than 95%. On the other hand, if the average rate of
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26/56 cooling in the second temperature range is less than 100 ° C / s, the transformation of ferrite and / or the transformation of perlite occurs so that it is not possible to make the total of the area fraction of martensite and the area fraction of bainite be no less than 95%. Therefore, the average cooling rate in the second temperature range is not less than 100 ° C / s. In addition, in the second temperature range, iron-based carbides are liable to precipitate in the grain boundary and the coverage factor of the grain boundary by iron-based carbides increases as the cooling time period in the second temperature range increases. For this reason, in order to make the coverage factor to be no more than 80%, the cooling time period in the second temperature range is preferably shorter. Also from this point of view, it is very effective to make the average cooling rate in the second temperature range to be no less than 100 ° C / s. To obtain the desired structure with certainty, the average cooling rate in the second temperature range is preferably not less than 150 ° C / s, and more preferably not less than 200 ° C / s. An upper limit on the average cooling rate in the second temperature range is not particularly specified, and, in an industrial sense, a range of no more than 500 ° C / s is practical. Here, the average cooling rate in the second temperature range is a value obtained by dividing the difference between the Ar3 point and (Ms - 50 point) ° C by the period of time that the cooling takes. Third temperature range [00155] In the third temperature range (from (point Ms - 50) ° C to 10 ° C), iron-based oxides are liable to precipitate in grains from the previous austenite, as described above. Making the carbides based on iron precipitate in the grains allows to obtain excellent toughness at low temperature. When the average cooling rate in the third temperature range is greater than 50 ° C / s, precipitation
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27/56 in grains is deficient, resulting in the fact that a large amount of dissolved C remains in the steel plate, thus deteriorating the toughness at low temperature. Therefore, the average cooling rate in the third temperature range is no more than 50 ° C / s. To obtain the desired structure with certainty, the average cooling rate in the third temperature range is preferably not more than 30 ° C / s, and more preferably not more than 20 ° C / s.
[00156] Even if the average cooling rate is no more than 50 ° C / s, when the cooling rate in a temperature range from (point Ms - 120) ° C to 100 ° C in the third temperature range is higher than 70 ° C / s, precipitation in the grains from the previous austenite is deficient, making it impossible to achieve a sufficient low temperature toughness. Therefore, the maximum cooling rate in the temperature range from (point Ms - 120) ° C to 100 ° C is no more than 70 ° C / s. In addition, even if the average cooling rate is no more than 50 ° C / s, when the cooling rate in a temperature range from (point Ms - 120) ° C to 100 ° C in the third temperature range is less than 5 ° C / s, the ferrite precipitates excessively during cooling, and it is not possible to make the total fraction of the martensite area and the fraction of the bainite area to be no less than 95%. In addition, the iron-based carbides that precipitate in a grain boundary increase so that the coverage factor of the grain boundary by iron-based oxides is greater than 80%. Therefore, the minimum cooling rate in the temperature range from (point Ms - 120) ° C to 100 ° C is no less than 5 ° C / s.
Fourth temperature range [00157] In the fourth temperature range (less than 100 ° C), since the precipitation of iron-based carbides is very unlikely to occur, and also the transformation does not occur, as described above, there is no the need to control in particular the rate of
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28/56 cooling.
[00158] Thus, it is possible to produce a hot stamped part according to the present modality, which has excellent resistance and tenacity at low temperature.
[00159] According to the production method of the hot stamped part according to the present modality, once an adequate temperature control is performed, it is possible to obtain a hot stamped part having an adequate structure, thus achieving excellent tensile strength and low temperature toughness.
[00160] Other conditions of forming by hot stamping, such as the type of forming and the type of mold, can be properly selected within a range that does not affect the effects of the present modality. For example, the type of forming can include folding, stamping, bulging, hole expansion, and flange forming. The type of mold can be selected appropriately depending on the type of forming.
[00161] The steel sheet for hot stamping can be a hot-rolled steel sheet or a cold-rolled steel sheet. An annealed hot-rolled steel sheet or an annealed cold-rolled steel sheet, which is obtained by subjecting the hot-rolled steel sheet or the cold-rolled steel sheet to annealing, can also be used as a steel sheet for hot stamping.
[00162] The steel sheet for hot stamping can be a steel sheet with a treated surface such as a coated steel sheet. That is, a steel sheet for hot stamping can be provided with a coating layer. The coating layer helps to increase, for example, corrosion resistance. The coating layer can be an electrocoating layer or a hot dip coating layer. A CA
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29/56 electrocoating layer is exemplified by an electroplating layer, and an electrocoating layer of a Zn-Ni alloy layer. The hot dip coating layer is exemplified by a hot dip galvanizing layer, a bonded hot dip galvanizing layer, a hot dip aluminum coating layer, a Zn-Al alloy coating layer by hot dip, a layer of Zn-Al-Mg alloy coating by hot dip, and a layer of Zn-Al-Mg-Si alloy coating by hot dip. The coating weight of the coating layer is not particularly limited, and can be, for example, a coating weight within a common range. The coating layer is supplied in a heat-treated material in the same way as in a steel plate for heat treatment.
[00163] Subsequently, an example of a method of producing a steel sheet for hot stamping will be described. In the production method, casting, hot rolling, pickling, cold rolling, annealing and coating treatment are carried out to produce a coated steel sheet, for example. [00164] In the casting, a plate is cast from a molten steel having the chemical composition described above. Like the slab, a continuous caster slab and a slab produced by a thin slab caster can be used. A process such as a continuous casting-direct lamination (CC-DR) process can be applied, in which hot rolling is performed immediately after the plate is cast.
[00165] The temperature of the plate before hot rolling (heating temperature of the plate) is preferably not more than 1300 ° C. If the heating temperature of the plate is excessively high, not only will the productivity deteriorate, but also the cost of
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30/56 production increases. Therefore, the heating temperature of the plate is preferably not more than 1250 ° C. When the heating temperature of the plate is less than 1050 ° C, the foot temperature will decrease in the finishing lamination, thus increasing the lamination load. As a result, not only can the rolling capacity deteriorate, but shape defects can also occur on the steel sheet. Therefore, the heating temperature of the plate is preferably not less than 1050 ° C.
[00166] The temperature of the finishing lamination (temperature of the finishing lamination) in the hot lamination is preferably not less than 850 ° C. When the temperature of the finishing laminate is less than 850 ° C, the laminating load can increase, which means that not only can laminating be difficult, but also defects in shape can occur in the steel plate. The upper limit of the finishing laminating temperature is not particularly specified, and the finishing laminating is preferably carried out at no more than 1000 ° C. This is because, when the temperature of the finishing laminate is greater than 1000 ° C, the heating temperature of the plate is raised excessively to obtain a temperature of more than 1000 ° C.
[00167] The temperature in the winding of the hot rolled steel sheet (winding temperature) after the end of the hot rolling is preferably not more than 700 ° C. When the coiling temperature is greater than 700 ° C, a thick oxide can be formed on the surface of the hot-rolled steel sheet, deteriorating its pickling property. When cold rolling is carried out after winding, the winding temperature is preferably not less than 600 ° C. This is because when the winding temperature is less than 600 ° C, the resistance of the hot rolled steel sheet may increase excessively, causing
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31/56 yes, sheet breakage and shape defects during cold rolling. Raw sheets after roughing lamination can be joined during hot rolling to perform the finishing lamination in a continuous manner. In addition, finishing lamination can be carried out after winding the raw laminated sheet once.
[00168] Oxides on the surface of the hot-rolled steel plate are removed by pickling. Stripping is particularly important for improving hot-dip coating capacity when producing a hot-dip coated steel sheet, such as a hot-dip coated aluminum sheet, a dip-galvanized steel sheet hot, hot-dip galvanized steel plate, and the like. The number of times blasting is carried out can be one or more times.
[00169] In cold rolling, for example, the lamination reduction ratio is 30% to 90%. When the rolling reduction ratio is less than 30%, it can be difficult to maintain the flat shape of the cold rolled steel sheet. In addition, it is sometimes difficult to achieve sufficient ductility after cold rolling. When the lamination reduction ratio is greater than 90%, the lamination load increases excessively, making cold lamination difficult. To achieve more excellent ductility, the lamination reduction ratio is preferably not less than 40%, and to achieve more excellent lamination capacity, the lamination reduction ratio is preferably no more than 70%. The number of rolling passes in cold rolling, and the reduction ratio for each pass are not particularly limited.
[00170] Annealing is carried out, for example, in a continuous annealing line or a box-type oven. The annealing condition is not particularly limited, and is preferably in
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32/56 a level that allows the cold rolled steel plate to be properly softened. For example, the annealing temperature is preferably within the range of 550 ° C to 850 ° C. By performing annealing within this temperature range, the displacements introduced during cold rolling are alleviated by recovery, recrystallization, and / or phase transformation. [00171] As a coating treatment, for example, a hot dip coating treatment or an electrocoating treatment is performed. The hot dip coating treatment includes a hot dip aluminum coating treatment, a hot dip galvanizing treatment, an alloy hot dip coating treatment, and a hot dip galvanizing treatment. switched on. According to the hot dip coating treatment, it is possible to achieve effects such as inhibiting scale formation and increasing corrosion resistance. To inhibit scale formation in a hot stamped part, a thicker coating layer is more preferable. To form a thicker coating layer, a hot dip galvanizing treatment is more preferable than the electrocoating treatment. Ni, Cu, Cr, Co, Al, Si or Zn, or any of their combinations can be included in a coating layer formed by the coating treatment. In addition, to improve the adhesion of the coating, a coating layer of Ni, Cu, Co or Fe, or any of their combinations can be formed on the cold rolled steel sheet before annealing.
[00172] Note that all the modalities described above show merely examples for the practice of the present invention, and these should not be interpreted as limiting the technical scope of the present invention. That is, the present invention can be practiced
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33/56 in several ways without leaving its technical concept or its main characteristics.
Examples [00173] Subsequently, an example of the present invention will be described. The condition shown in the example merely indicates a condition that is adopted to confirm the feasibility and effect of the present invention, and the present invention will not be limited to the example of that condition. The present invention can adopt several conditions as long as its objective is achieved without departing from the essence of the present invention.
[00174] In this experiment, plates were cast using steel (aare types A to H) with the chemical compositions listed in table 1, and hot rolling was performed under the conditions listed in Tables 2 and 3. For some of the hot-rolled steel sheets, cold rolling was performed after hot rolling. For some of the cold rolled steel sheets, the coating treatment was carried out by continuous annealing equipment or continuous hot dip coating equipment after cold rolling. In this way, several steel sheets for hot stamping were prepared (a hot-rolled steel sheet, a cold-rolled steel sheet, a hot-dip galvanized steel sheet, a hot-dip galvanized steel sheet bonded , or a hot-dip coated aluminum sheet). Under a condition in which a hot-rolled steel sheet was used as a hot-stamping steel sheet, the thickness of the hot-rolled steel sheet was 1.6 mm. Under a condition in which the steel plate other than the hot-rolled steel plate was used as the hot-stamping steel plate, the thickness of the hot-rolled steel plate was 3.2 mm, the rolling reduction ratio d cold rolling was 50%, and the
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34/56 thickness of the cold rolled steel sheet was 1.6 mm. Blanks in Table 1 indicate that the content of the corresponding element was less than the detection limit. Data underlined in Table 1, 2, or 3 indicate that yours was outside the scope of the present invention.
[00175] After the hot stamping steel sheet was prepared, the hot stamping was performed under the conditions listed in Tables 4 and 5 to obtain the hot stamped part. In Tables 4 and 5, the minimum cooling rate indicates the minimum cooling rate in a temperature range from (point Ms - 120) ° C to 100 ° C, and the maximum cooling rate indicates the maximum rate of cooling cooling in the temperature range from (point Ms - 120) ° C to 100 ° C. A value underlined in Tables 4 and 5 indicates that its numerical value was outside the scope of the present invention.
[00176] Then, the measurement of the tensile property, the observation of the structure, and the evaluation of the tenacity at low temperature, for each by the hot stamping were performed.
[00177] In measuring the tensile property, a tensile test specimen according to JIS Z 2201 was taken, and a tensile test was performed in accordance with JIS Z 2241 to measure the tensile strength. These results are listed in Tables 6 and 7. An underlined value in Table 6 or 7 indicates that the numerical value is outside a desired range in the present invention.
[00178] In the observation of the structure, the fraction of the martensite area, the fraction of the bainite area, the fraction of the ferrite area, and the fraction of the retained austenite area, the covering factor of the austenite grain contour were measured the former by the iron-based carbides and the numerical density of the iron-based carbides in the austenite grains.
[00179] The area fraction of martensite, the area fraction of bainite,
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35/56 and the fraction of ferrite area were determined by taking a sample that had a cross section in parallel with the rolling direction and the direction of the thickness of the hot stamped part as an observation surface, polishing the surface observation, executing caustication with Nital, and observing the portion of the steel plate at a depth of 1/8 to 3/8 of its thickness with an FE-SEM. In the observation, the fractions of area of each structure were measured in 10 visual fields at a magnification of 5000 times for a hot stamped part, and its average value was adopted as the area fraction of each structure in the hot stamped part. The fraction of area of the retained austenite was determined from an X-ray diffraction intensity ratio between ferrite and austenite. Perlite was not observed.
[00180] The grain contour coverage factor of the previous austenite by the carbides based on iron was obtained by the method described in relation to Figure 1. That is, for each hot stamped part, the value represented by (X / L) x 100 (%) was determined.
[00181] In assessing low temperature toughness, a Charpy impact test was performed at -120 ° C. Then the evaluation was made so that the result was classified as approved (O) when it presented an energy absorption, which was obtained by converting the measured absorption energy to that of a specimen having a thickness of 10 mm, of not less than 50 J / cm ² and a ductile fracture percentage of not less than 50%, and was classified as a failure (x) when it did not satisfy one or both of the above.
[00182] As listed in Tables 6 and 7, in the examples of the invention, in which all conditions were within the scope of the present invention, it was possible to achieve a tensile strength of not less than 1180 MPa and excellent low temperature toughness. On the other hand, in comparative examples, in which any one or
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36/56 more types of conditions were outside the scope of the present invention, it was not possible to achieve a tensile strength of not less than 1180 MPa and / or excellent low temperature toughness.
[00183] In conditions a-7, b-7, c-7, n-7, and q-7, since the heating temperature of the hot stamping was very low, the fractions of area of martensite and bainite have been deficient so that the desired tensile strength has not been achieved.
[00184] Under conditions a-8, b-8, c-8, n-8, and q-8, since the average cooling rate in the second temperature range was very low, the fractions of area of martensite and bainite were deficient so that the desired tensile strength was not achieved. In addition, the coverage factor for iron-based carbides increased so that excellent low temperature toughness was not achieved.
[00185] Under conditions a-9, b-9, c-9, n-9, and q-9, since the minimum cooling rate in the temperature range since (point Ms 120) ° C was low, the fractions of area of martensite and bainite were deficient in the hot stamped part so that the desired tensile strength was not achieved. In addition, the iron-based carbide coverage factor has increased so that excellent low temperature toughness has not been achieved.
[00186] In conditions a-10, b-10, c-10, n-10, and q-10, since the maximum rate in a temperature range from (point Ms 120) ° C to 100 ° C in hot stamping was very high, the precipitation of iron-based carbides in the grains of the previous austenite was deficient, so that the excellent tenacity at low temperature was not achieved.
[00187] Under conditions a-11, b-11, c-11, n-11, and q-11, since the average cooling rate in a third temperature range in hot stamping was very high, precipitation of carbides
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37/56 iron-based grains from the previous austenite was deficient so that excellent low temperature toughness was not achieved. [00188] In conditions A-1, B-1, C-1, D-1, E-1, F-1, G-1, and H-1, since the chemical compositions were outside the scope of this invention, tensile strength of not less than 1180 MPa and / or excellent low temperature toughness has not been achieved. For example, in condition B1, the C content was very high so that the resistance was excessively high and an excellent tenacity at low temperature was not achieved. In the F1 condition, since the total content of Mn and Cr was very high, excellent tenacity at low temperature was not achieved.
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Table 1
Steel type Chemical composition (% by mass) Ac3 (° C) Ar3 (° C) Ms(° C) Grades Ç Si Al Mn Cr B P s N O You Nb V Ni Ass Mo Here REM The 0.128 0.010 0.011 1.22 0.21 0.0005 0.004 0.0011 0.0026 0.0012 806 738 456 Ex. Invention B 0.149 0.180 0.013 2.69 0.22 0.0009 0.007 0.0014 0.0028 0.0011 767 601 398 Ex. Invention ç 0.221 0.280 0.015 1.32 0.19 0.0007 0.005 0.0015 0.0033 0.0009 793 705 405 Ex. Invention d 0.229 0.180 0.029 1.25 1.38 0.0039 0.019 0.0033 0.0045 0.0024 793 654 388 Ex. Invention and 0.242 1,150 0.075 2.49 0.33 0.0004 0.011 0.0023 0.0025 0.0008 0.029 833 616 359 Ex. Invention f 0.229 0.130 0.033 1.56 0.17 0.0008 0.009 0.0038 0.0030 0.00120.059 789 680 398 Ex. Invention g 0.235 0.110 0.029 1.25 0.20 0.0009 0.013 0.0027 0.0024 0.0018 0.056803 704 405 Ex. Invention H 0.246 0.250 0.015 1.49 0.42 0.0008 0.010 0.0024 0.0020 0.0010 0.019 0.011 792 673 388 Ex. Invention i 0.229 0.030 0.006 1.29 0.20 0.0010 0.012 0.0029 0.0029 0.0013 0.29 780 686 402 Ex. Invention j 0.228 0.220 0.028 1.35 0.20 0.0016 0.009 0.0030 0.0025 0.0014 0.32 791 686 405 Ex. Invention k 0.233 0.060 0.033 1.35 0.21 0.0008 0.008 0.0022 0.0024 0.00090.42 804 674 394 Ex. Invention l 0.230 0.320 0.014 1.65 0.18 0.0012 0.014 0.0027 0.0040 0.0010 0.0045791 677 394 Ex. Invention m 0.229 0.480 0.039 2.02 0.85 0.0021 0.012 0.0038 0.0029 0.0013 0.0029 788 617 371 Ex. Invention n 0.282 1,570 0.005 1.46 0.25 0.0019 0.008 0.0015 0.0024 0.0019 833 715 375 Ex. Invention O 0.284 0.380 0.007 1.88 0.22 0.0004 0.009 0.0019 0.0016 0.0007 0.024 0.014 779 638 361 Ex. Invention P 0.279 0.180 0.014 1.24 0.68 0.0008 0.001 0.0022 0.0029 0.0014 0.024 0.22 782 661 372 Ex. Invention q 0.332 0.320 0.042 1.42 0.69 0.0009 0.006 0.0009 0.0021 0.0009 778 641 345 Ex. Invention r 0.388 0.480 0.032 1.68 0.18 0.0007 0.009 0.0019 0.0025 0.0011 0.0580.029 0.31 808 614 312 Ex. Invention THE 0.078 0.320 0.032 1.13 0.19 0.0007 0.012 0.0038 0.0030 0.0024 853 774 484 Ex. Comp. B 0.607 0.410 0.024 1.32 0.22 0.0004 0.008 0.0021 0.0024 0.0016 743 586 226 Ex. Comp. Ç 0.253 2,080 0.211 1.22 0.32 0.0011 0.010 0.0023 0.0032 0.0022 952 760 395 Ex. Comp. D 0.233 0.330 0.112 1.29 0.55 0.0024 0.008 0.0019 0.0024 0.0010 832 692 399 Ex. Comp. AND 0.155 0.480 0.045 0.45 0.12 0.0016 0.006 0.0024 0.0027 0.0008 859 820 471 Ex. Comp. F 0.234 0.510 0.032 2.45 1.68 0.0008 0.022 0.0026 0.0026 0.0023 771 539 341 Ex. Comp. G 0.229 0.880 0.028 0.84 0.40 0.0000 0.021 0.0028 0.0031 0.0016 848 760 418 Ex. Comp. H 0.232 0.420 0.012 1.36 0.20 0.0007 0.092 0.0020 0.0019 0.0024 857 705 403 Ex. Comp.
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Table 2
Condition Steel type Type of steel sheet for hot stamping Hot rolling Grades Plate heating temperature (° C) Finishing temperature (° C) Coiling temperature (° C) to 1 The Hot rolled steel sheet 1220 870 440 Ex. Invention a-2 The Cold rolled steel sheet 1250 890 550 Ex. Invention a-3 The Hot-dip galvanized steel sheet 1240 920 600 Ex. Invention a-4 The Hot-dip galvanized steel sheet bonded 1230 880 620 Ex. Invention a-5 The Hot-dip coated aluminum sheet steel 1220 900 590 Ex. Invention a-6 The Hot-dip coated aluminum sheet steel 1220 930 600 Ex. Invention a-7 The Hot-dip coated aluminum sheet steel 1210 910 600 Comparative example a-8 The Hot-dip coated aluminum sheet steel 1190 900 620 Comparative example a-9 The Cold rolled steel sheet 1250 880 600 Comparative example a-10 The Hot-dip coated aluminum sheet steel 1180 900 570 Comparative example a-11 The Hot-dip coated aluminum sheet steel 1200 900 600 Comparative example b-1 B Hot rolled steel sheet 1210 940 520 Ex. Invention b-2 B Cold rolled steel sheet 1200 890 590 Ex. Invention b-3 B Hot-dip galvanized steel sheet 1200 930 600 Ex. Invention
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Condition Steel type Type of steel sheet for hot stamping Hot rolling Grades Plate heating temperature (° C) Finishing temperature (° C) Coiling temperature (° C) b-4 B Hot-dip galvanized steel sheet bonded 1220 900 620 Ex. Invention b-5 B Hot-dip galvanized steel sheet 1230 910 580 Ex. Invention b-6 B Hot-dip galvanized steel sheet 1240 930 610 Ex. Invention b-7 B Hot-dip galvanized steel sheet 1200 910 590 Comparative example b-8 B Hot-dip galvanized steel sheet 1200 920 630 Comparative example b-9 B Cold rolled steel sheet 1250 880 600 Comparative example b-10 B Hot-dip coated aluminum sheet steel 1180 900 570 Comparative example b-11 B Hot-dip coated aluminum sheet steel 1200 900 600 Comparative example c-1 ç Hot rolled steel sheet 1230 900 600 Ex. Invention c-2 ç Cold rolled steel sheet 1200 910 590 Ex. Invention c-3 ç Hot-dip galvanized steel sheet 1210 920 600 Ex. Invention c-4 ç Hot-dip galvanized steel sheet bonded 1200 900 610 Ex. Invention c-5 ç Hot-dip galvanized steel sheet 1180 900 620 Ex. Invention c-6 ç Hot-dip galvanized steel sheet 1230 930 600 Ex. Invention
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Condition Steel type Type of steel sheet for hot stamping Hot rolling Grades Plate heating temperature (° C) Finishing temperature (° C) Coiling temperature (° C) c-7 ç Hot-dip galvanized steel sheet 1270 880 590 Comparative example c-8 ç Hot-dip galvanized steel sheet 1200 910 580 Comparative example c-9 ç Cold rolled steel sheet 1200 880 600 Comparative example c-10 ç Hot-dip coated aluminum sheet steel 1200 900 570 Comparative example c-11 ç Hot-dip coated aluminum sheet steel 1200 900 600 Comparative example d-1 d Cold rolled steel sheet 1220 870 620 Ex. Invention d-2 d Hot-dip galvanized steel sheet 1230 950 600 Ex. Invention e-1 and Cold rolled steel sheet 1270 970 630 Ex. Invention f-1 f Cold rolled steel sheet 1260 950 600 Ex. Invention g-1 g Cold rolled steel sheet 1260 980 600 Ex. Invention h-1 H Cold rolled steel sheet 1280 960 590 Ex. Invention i-1 i Cold rolled steel sheet 1230 910 610 Ex. Invention
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Table 3
Condition Steel type Hot stamping steel type Hot rolling Grades Plate heating temperature (° C) Finishing temperature (° C) Coiling temperature (° C) j-1 j Cold rolled steel sheet 1200 900 580 Ex. Invention k-1 k Cold rolled steel sheet 1200 930 600 Ex. Invention l-1 l Cold rolled steel sheet 1210 940 600 Ex. Invention m-1 m Cold rolled steel sheet 1230 920 590 Ex. Invention n-1 n Hot rolled steel plate 1220 910 630 Ex. Invention n-2 n Cold rolled steel sheet 1240 920 650 Ex. Invention n-3 n Hot-dip galvanized steel sheet 1210 920 650 Ex. Invention n-4 n Hot-dip galvanized steel sheet bonded 1200 890 630 Ex. Invention n-5 n Hot-dip galvanized steel sheet 1220 900 580 Ex. Invention n-6 n Hot-dip galvanized steel sheet 1230 920 570 Ex. Invention n-7 n Hot-dip galvanized steel sheet 1240 930 600 Comparative example n-8 n Hot-dip galvanized steel sheet 1200 930 620 Comparative example n-9 n Cold rolled steel sheet 1250 880 600 Comparative example
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Condition Steel type Hot stamping steel type Hot rolling Grades Plate heating temperature (° C) Finishing temperature (° C) Coiling temperature (° C) n-10 n Hot-dip coated aluminum sheet steel 1180 900 570 Comparative example n-11 n Hot-dip coated aluminum sheet steel 1200 900 600 Comparative example o-1 O Hot-dip galvanized steel sheet 1270 960 590 Ex. Invention p-1 P Hot-dip galvanized steel sheet 1250 940 650 Ex. Invention q-1 q Hot rolled steel sheet 1180 880 470 Ex. Invention q-2 q Cold rolled steel sheet 1210 900 590 Ex. Invention q-3 q Hot-dip galvanized steel sheet 1230 920 590 Ex. Invention q-4 q Hot-dip galvanized steel sheet bonded 1220 910 620 Ex. Invention q-5 q Hot-dip galvanized steel sheet 1220 910 630 Ex. Invention q-6 q Hot-dip galvanized steel sheet 1230 890 630 Ex. Invention q-7 q Hot-dip galvanized steel sheet 1230 920 640 Comparative example q-8 q Hot-dip galvanized steel sheet 1210 930 600 Comparative example
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Condition Steel type Hot stamping steel type Hot rolling Grades Plate heating temperature (° C) Finishing temperature (° C) Coiling temperature (° C) q-9 q Hot-dip galvanized steel sheet 1250 880 600 Comparative example q-10 q Steel sheet coated with aluminum or hot dip 1180 900 570 Comparative example q-11 q Steel sheet coated with aluminum or hot dip 1200 900 600 Comparative example r-1 r Steel sheet coated with aluminum or hot dip 1280 920 620 Ex. Invention TO 1 THE Cold rolled steel sheet 1230 920 630 Comparative example B-1 B Cold rolled steel sheet 1210 930 620 Comparative example C-1 Ç Cold rolled steel sheet 1240 940 590 Comparative example D-1 D Cold rolled steel sheet 1230 900 600 Comparative example E-1 AND Cold rolled steel sheet 1200 910 600 Comparative example F-1 F Cold rolled steel sheet 1210 920 620 Comparative example G-1 G Cold rolled steel sheet 1210 930 630 Comparative example H-1 H Cold rolled steel sheet 1230 920 640 Comparative example
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Table 4
Condition Hot pressing Grades Heating rate (° C / s) Heating temperature (° C) Average cooling rate in the second temperature range (° C / s) Average cooling rate in the third temperature range (° C / s) Minimum cooling rate (° C / s) Maximum cooling rate (° C / s) to 1 6 910 160 35 10 60 Ex. Invention a-2 4 930 120 30 5 50 Ex. Invention a-3 5 920 240 50 10 50 Ex. Invention a-4 10 920 160 45 20 70 Ex. Invention a-5 6 900 110 45 10 60 Ex. Invention a-6 7 920 220 50 5 70 Ex. Invention a-7 5 740 160 40 30 60 Comparative example a-8 6 890 80 40 10 60 Comparative example a-9 10 900 100 50 3 60 Comparative example a-10 5 900 150 50 5 80 Comparative example a-11 5 900 120 55 10 60 Comparative example b-1 5 880 200 35 10 60 Ex. Invention b-2 6 890 180 30 5 50 Ex. Invention b-3 8 870 180 50 10 50 Ex. Invention b-4 4 890 160 45 20 70 Ex. Invention b-5 5 880 200 45 10 60 Ex. Invention
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Condition Hot pressing Grades Heating rate (° C / s) Heating temperature (° C) Average cooling rate in the second temperature range (° C / s) Average cooling rate in the third temperature range (° C / s) Minimum cooling rate (° C / s) Maximum cooling rate (° C / s) b-6 12 920 230 50 5 70 Ex. Invention b-7 6 700 160 40 30 60 Comparative example b-8 7 900 60 40 10 60 Comparative example b-9 10 900 100 50 3 60 Comparative example b-10 5 900 150 50 5 80 Comparative example b-11 5 900 120 55 10 60 Comparative example c-1 8 920 180 20 10 60 Ex. Invention c-2 4 930 160 50 5 50 Ex. Invention c-3 6 900 160 45 10 50 Ex. Invention c-4 5 940 150 40 20 70 Ex. Invention c-5 3 930 180 50 10 60 Ex. Invention c-6 9 900 230 30 5 70 Ex. Invention c-7 5 720 120 30 30 60 Comparative example c-8 6 910 40 25 10 60 Comparative example c-9 10 900 100 50 2 60 Comparative example c-10 5 900 150 50 5 100 Comparative example c-11 5 900 120 55 10 60 Comparative example
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Condition Hot pressing Grades Heating rate (° C / s) Heating temperature (° C) Average cooling rate in the second temperature range (° C / s) Average cooling rate in the third temperature range (° C / s) Minimum cooling rate (° C / s) Maximum cooling rate (° C / s) d-1 5 910 120 30 10 60 Ex. Invention d-2 6 940 220 40 10 50 Ex. Invention e-1 5 950 150 35 5 70 Ex. Invention f-1 6 920 140 30 5 60 Ex. Invention g-1 12 920 150 35 20 50 Ex. Invention h-1 6 930 150 30 20 60 Ex. Invention i-1 4 920 160 30 5 70 Ex. Invention
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Table 5
Condition Hot pressing Grades Heating rate (° C / s) Heating temperature (° C) Average cooling rate in the second temperature range (° C / s) Average cooling rate in the third temperature range (° C / s) Minimum cooling rate (° C / s) Maximum cooling rate (° C / s) i-1 4 920 160 30 10 50 Ex. Invention j-1 5 910 160 30 5 70 Ex. Invention k-1 6 920 150 35 15 60 Ex. Invention l-1 8 910 150 30 10 60 Ex. Invention m-1 4 930 160 10 10 70 Ex. Invention n-1 5 900 120 20 10 60 Ex. Invention n-2 6 920 150 40 5 50 Ex. Invention n-3 7 920 150 40 10 50 Ex. Invention n-4 10 910 140 35 20 70 Ex. Invention n-5 5 910 160 30 30 60 Ex. Invention n-6 5 930 220 40 10 60 Ex. Invention n-7 6 710 110 30 30 60 Comparative example n-8 7 930 50 30 10 60 Comparative example n-9 10 900 100 50 3 60 Comparative example n-10 5 900 150 50 5 120 Comparative example n-11 5 900 120 55 10 60 Comparative example
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Condition Hot pressing Grades Heating rate (° C / s) Heating temperature (° C) Average cooling rate in the second temperature range (° C / s) Average cooling rate in the third temperature range (° C / s) Minimum cooling rate (° C / s) Maximum cooling rate (° C / s) o-1 5 920 140 10 10 60 Ex. Invention p-1 11 930 170 40 5 70 Ex. Invention q-1 7 930 150 45 10 60 Ex. Invention q-2 5 910 160 40 5 50 Ex. Invention q-3 9 930 140 30 10 50 Ex. Invention q-4 8 920 150 45 20 70 Ex. Invention q-5 6 920 150 30 10 60 Ex. Invention q-6 7 930 220 40 5 70 Ex. Invention q-7 8 720 140 40 30 60 Comparative example q-8 6 920 40 30 10 60 Comparative example q-9 10 900 100 50 2 60 Comparative example q-10 5 900 150 50 5 90 Comparative example q-11 5 900 120 55 10 60 Comparative example r-1 7 940 200 40 5 60 Ex. Invention TO 1 5 930 160 40 10 70 Comparative example B-1 12 920 250 50 20 70 Comparative example C-1 7 950 120 35 30 60 Comparative example
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Condition Hot pressing Grades Heating rate (° C / s) Heating temperature (° C) Average cooling rate in the second temperature range (° C / s) Average cooling rate in the third temperature range (° C / s) Minimum cooling rate (° C / s) Maximum cooling rate (° C / s) D-1 5 950 80 30 5 60 Comparative example E-1 8 940 200 40 10 70 Comparative example F-1 6 920 160 35 20 70 Comparative example G-1 8 930 170 35 30 50 Comparative example H-1 7 950 150 30 5 50 Comparative example
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Table 6
Condition Steel type Area fraction Iron-based carbide Tensile strength(MPa) Low temperature toughness Grades Vm (%) Vb (%) T _F (%) V _r R (%) Vm + Vb(%) Coverage factor(%) Numerical density (/ pm ² ) to 1 The 78 18 0 4 96 63 70 1213 O Ex. Invention a-2 The 70 27 0 3 97 71 67 1181 O Ex. Invention a-3 The 96 1 0 3 97 10 65 1235 O Ex. Invention a-4 The 79 17 0 4 96 65 72 1207 O Ex. Invention a-5 The 72 25 0 3 97 75 75 1122 O Ex. Invention a-6 The 98 0 0 2 98 33 54 1261 O Ex. Invention a-7 The 54 21 17 8 75 30 72 978 O Comparative example a-8 The 48 40 12 0 88 85 94 897 X Comparative example a-9 The 38 27 35 0 65 85 85 758 X Comparative example a-10 The 80 20 0 0 100 10 28 1310 X Comparative example a-11 The 85 15 0 0 100 15 35 1285 X Comparative example b-1 B 84 12 0 4 96 24 75 1356 O Ex. Invention b-2 B 80 17 0 3 97 25 72 1326 O Ex. Invention b-3 B 84 13 0 3 97 25 71 1379 O Ex. Invention b-4 B 87 11 0 2 98 31 78 1349 O Ex. Invention b-5 B 86 12 0 2 98 20 80 1372 O Ex. Invention b-6 B 96 0 0 4 96 14 59 1358 O Ex. Invention
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Condition Steel type Area fraction Iron-based carbide Tensile strength(MPa) Low temperature toughness Grades Vm (%) Vb (%) T _F (%) V _r R (%) Vm + Vb(%) Coverage factor(%) Numerical density (/ pm ² ) b-7 B 42 18 10 30 60 64 77 952 O Comparative example b-8 B 48 43 0 9 91 82 100 1012 X Comparative example b-9 B 38 27 35 0 65 85 90 882 X Comparative example b-10 B 80 20 0 0 100 10 33 1310 X Comparative example b-11 B 85 15 0 0 100 15 39 1331 X Comparative example c-1 ç 78 20 0 2 98 33 80 1472 O Ex. Invention c-2 ç 97 0 0 3 97 45 77 1496 O Ex. Invention c-3 ç 87 10 0 3 97 42 75 1482 O Ex. Invention c-4 ç 91 8 0 1 99 40 82 1486 O Ex. Invention c-5 ç 92 7 0 1 99 35 86 1488 O Ex. Invention c-6 ç 99 0 0 1 99 22 62 1509 O Ex. Invention c-7 ç 43 12 37 8 55 73 82 975 O Comparative example c-8 ç 59 31 10 0 90 87 112 1112 X Comparative example c-9 ç 42 40 18 0 82 95 105 921 X Comparative example c-10 ç 85 15 0 0 100 12 35 1532 X Comparative example c-11 ç 85 15 0 0 100 15 42 1543 X Comparative example d-1 d 88 8 0 4 96 75 78 1534 O Ex. Invention d-2 d 98 0 0 2 98 15 82 1509 O Ex. Invention
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Condition Steel type Area fraction Iron-based carbide Tensile strength(MPa) Low temperature toughness Grades Vm (%) Vb (%) Vf (%) V _r R (%) 1 Vm + Vb(%) Coverage factor(%) Numerical density (/ pm ² ) 94 e-1 and 84 15 0 99 55 1512 O Ex. Invention f-1 f 87 11 0 2 98 65 91 1522 O Ex. Invention g-1 g 86 12 0 2 98 50 88 1533 O Ex. Invention h-1 H 80 18 0 2 98 52 97 1548 O Ex. Invention i-1 i 83 16 0 1 99 50 93 1512 O Ex. Invention
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Table Ί
Condition Steel type Area fraction Iron-based carbide Tensile strength(MPa) Low temperature toughness Grades Vm (%) Vb (%) T _F (%) V _YR (%) Vm + Vb(%) Coverage factor(%) Numerical density (/ pm ² ) j-1 j 87 11 0 2 98 55 89 1529 O Ex. Invention k-1 k 82 16 0 2 98 60 95 1544 O Ex. Invention l-1 l 84 15 0 1 99 50 93 1531 O Ex. Invention m-1 m 81 17 0 2 98 48 96 1552 O Ex. Invention n-1 n 75 24 0 1 99 64 118 1782 O Ex. Invention n-2 n 93 6 0 1 99 60 105 1821 O Ex. Invention n-3 n 95 4 0 1 99 60 101 1819 O Ex. Invention n-4 n 92 7 0 1 99 65 101 1832 O Ex. Invention n-5 n 93 5 0 2 98 60 100 1826 O Ex. Invention n-6 n 98 0 0 2 98 23 97 1792 O Ex. Invention n-7 n 37 4 52 7 41 50 122 1154 O Comparative example n-8 n 53 32 15 0 85 91 110 1152 X Comparative example n-9 n 38 54 8 0 92 92 118 1088 X Comparative example n-10 n 90 10 0 0 100 9 28 1833 X Comparative example n-11 n 85 15 0 0 100 15 35 1825 X Comparative example o-1 O 98 0 0 2 98 65 88 2016 O Ex. Invention p-1 P 93 4 0 3 97 64 103 1986 O Ex. Invention
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Condition Steel type Area fraction Iron-based carbide Tensile strength(MPa) Low temperature toughness Grades Vm (%) Vb (%) T _F (%) V _YR (%) Vm + Vb(%) Coverage factor(%) Numerical density (/ pm ² ) q-1 q 96 1 0 3 97 72 99 2024 O Ex. Invention q-2 q 94 3 0 3 97 61 100 1981 O Ex. Invention q-3 q 91 5 0 4 96 75 115 1970 O Ex. Invention q-4 q 96 1 0 3 97 65 108 2007 O Ex. Invention q-5 q 93 5 0 2 98 57 104 1978 O Ex. Invention q-6 q 99 0 0 1 99 15 92 1984 O Ex. Invention q-7 q 43 7 43 7 50 47 119 1176 O Comparative example q-8 q 68 21 11 0 89 85 98 1163 X Comparative example q-9 q 42 48 10 0 90 90 105 1241 X Comparative example q-10 q 100 0 0 0 100 10 35 2021 X Comparative example q-11 q 85 15 0 0 100 15 42 1994 X Comparative example r-1 r 96 2 0 2 98 20 131 2038 O Ex. Invention TO 1 THE 64 35 0 1 99 55 67 1075 O Comparative example B-1 B 96 0 0 4 96 10 138 2539 X Comparative example C-1 Ç 42 19 36 3 61 75 103 1124 O Comparative example D-1 D 52 12 30 6 64 75 99 1084 O Comparative example E-1 AND 33 44 20 3 77 20 67 993 O Comparative example F-1 F 96 0 0 4 96 50 41 1682 X Comparative example
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Condition Steel type Area fraction Iron-based carbide Tensile strength(MPa) Low temperature toughness Grades Vm (%) Vb (%) T _F (%) V _YR (%) Vm + Vb(%) Coverage factor(%) Numerical density (/ pm ² ) G-1 G 32 34 32 2 66 45 77 1073 O Comparative example H-1 H 63 21 13 3 84 55 67 1186 X Comparative example
Industrial applicability [00189] The present invention can be used for industries for the production and use, for example, of a hot stamped part used for automobiles, and others. The present invention can also be used for industries to produce and use another structural part and machine.

权利要求:
Claims (8)
[1]
1. Hot stamped part, characterized by the fact that it comprises:
a chemical composition consisting of, in% by mass, by:
C: 0.120% to 0.400%;
Si: 0.005% to 2,000%;
Mn or Cr, or both: 1.00% to 3.00% in total;
Al: 0.005% to 0.100%;
B: 0.0003% to 0.0020%;
P: no more than 0.030%;
S: not more than 0.0100%;
O: not more than 0.0070%;
N: not more than 0.0070%;
Ti: 0% to 0.100%;
Nb: 0% to 0.100%;
V: 0% to 0.100%;
Ni: 0% to 2.00%;
Cu: 0% to 2.00%;
Mo: 0% to 0.50%;
Ca or REM, or both: 0% to 0.0300% in total; and the balance: Fe and impurities; and a structure represented by:
a fraction of the area of martensite or bainite, or both: not less than 95% in total;
a covering factor of the grain outline of the previous austenite by carbides based on iron: no more than 80%; and numerical density of iron-based carbides in the grains of the previous austenite: not less than 45 / pm ² .
[2]
2. Stamped part according to claim 1, ca
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2/4 characterized by the fact that the chemical composition satisfies:
Ti: 0.005% to 0.100%;
Nb: 0.005% to 0.100%; or
V: 0.005% to 0.100%; or any of its combinations.
[3]
3. Stamped part, according to claim 1 or 2, characterized by the fact that the chemical composition satisfies:
Ni: 0.05% to 2.00%;
Cu: 0.05% to 2.00%; or
Mo: 0.05% to 0.50%; or any of its combinations.
[4]
4. Stamped part according to any one of claims 1 to 3, characterized by the fact that the chemical composition satisfies:
Ca or REM, or both: 0.0005% to 0.0300% in total.
[5]
5. Method of producing a hot stamped part, characterized by the fact that it comprises the steps of:
heat a steel sheet to a temperature of not less than the point Acs and not more than 950 ° C at an average heating rate of not less than 2 ° C / s;
then cool the steel sheet over a temperature range from the point Ars to (point Ms - 50) ° C at an average cooling rate of not less than 100 ° C / s while performing the hot pressing; and then cool the steel sheet over a temperature range of (Ms - 50 point) ° C to 100 ° C at an average cooling rate of no more than 50 ° C / s, where the steel sheet comprises a composition chemical consisting of, in% by mass, by:
C: 0.120% to 0.400%;
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Si: 0.005% to 2,000%;
Mn or Cr, or both: 1.00% to 3.00% in total;
Al: 0.005% to 0.100%;
B: 0.0003% to 0.0020%;
P: no more than 0.030%;
S: not more than 0.0100%;
O: not more than 0.0070%;
N: not more than 0.0070%;
Ti: 0% to 0.100%;
Nb: 0% to 0.100%;
V: 0% to 0.100%;
Ni: 0% to 2.00%;
Cu: 0% to 2.00%;
Mo: 0% to 0.50%;
Ca or REM, or both: 0% -0.0300% in total; and the balance: Fe and impurities, and the maximum cooling rate is no more than 70 ° C / s and the minimum cooling rate is no less than 5 ° C / s over a temperature range of (point Ms - 120) ° C to 100 ° C.
[6]
6. Method, according to claim 5, characterized by the fact that the chemical composition satisfies:
Ti: 0.005% to 0.100%;
Nb: 0.005% to 0.100%; or
V: 0.005% to 0.100%; or any of its combinations.
[7]
7. Method according to claim 5 or 6, characterized by the fact that the chemical composition satisfies:
Ni: 0.05% to 2.00%;
Cu: 0.05% to 2.00%; or
Mo: 0.05% to 0.50%; or
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4/4 any of its combinations.
[8]
8. Method according to any one of claims 5 to 7, characterized by the fact that the chemical composition satisfies:
Ca or REM or both: 0.0005% to 0.0300% in total.

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同族专利:

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公开号 | 公开日

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KR20160023855A|2016-03-03|

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US20160145704A1|2016-05-26|

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JPWO2015041159A1|2017-03-02|

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CA2916941A1|2015-03-26|

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CN105518173A|2016-04-20|

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MX2016000028A|2016-03-09|

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CN105518173B|2017-09-15|

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RU2016105443A|2017-10-23|

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TWI531667B|2016-05-01|

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TW201529868A|2015-08-01|

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JP6112211B2|2017-04-12|

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EP3020845A4|2017-04-05|

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PL3020845T3|2018-07-31|

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RU2648104C2|2018-03-22|

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BR112015032803A2|2017-07-25|

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EP3020845B1|2018-01-31|

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US10301699B2|2019-05-28|

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CA2916941C|2018-01-09|

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WO2015041159A1|2015-03-26|

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KR101753016B1|2017-07-03|

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EP3020845A1|2016-05-18|

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ES2662381T3|2018-04-06|

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法律状态:
2019-07-16| 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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2019-09-10| B25D| Requested change of name of applicant approved|Owner name: NIPPON STEEL CORPORATION (JP) |

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2019-12-24| B09A| Decision: intention to grant|

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2020-01-14| B16A| Patent or certificate of addition of invention granted|Free format text: PRAZO DE VALIDADE: 20 (VINTE) ANOS CONTADOS A PARTIR DE 12/09/2014, OBSERVADAS AS CONDICOES LEGAIS. |

优先权:

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申请号 | 申请日 | 专利标题

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JP2013193124|2013-09-18|

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PCT/JP2014/074184|WO2015041159A1|2013-09-18|2014-09-12|Hot stamp molded body and method for producing same|

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