• 专利附录
  • 专利说明
  • 权利要求
  • 类似技术
  • 同族专利
  • 引用文献
  • 法律状态
  • 优先权
    • 专利摘要:
    laser welding process for producing a semi-finished sheet product from hardenable steel with an aluminum or aluminium-silicon based coating. The invention relates to a process for producing a bespoke hot moldable sheet semi-finished steel product, in which at least two steel sheets (1, 2') of different grades of material quality and/or thickness are joined end to end by laser welding, at least one of the sheets being made of pressure curable steel and having a metallic coating (1.1, 2.1) based on aluminum or aluminium-silicon. the steel sheets (1, 2') are welded together, according to the invention, with a slot (g) limited by its edges to be welded together and having an average width (b) of at least 0 .15 mm, with so much material from the auxiliary wire (8) being introduced into the slit (g), that the ratio of the auxiliary wire volume introduced into the slit (g) to the volume of the molten material by means of a laser beam is hair minus 20%. the process according to the invention does not require prior roughing of the edge of the sheet edges to be welded and therefore offers considerable cost advantages.
    公开号:BR112018002126B1
    申请号:R112018002126-1
    申请日:2016-09-20
    公开日:2021-08-17
    发明作者:Arndt Breuer；Christian Both
    申请人:Wisco Tailored Blanks Gmbh；
    IPC主号:
    专利说明:

    [0001] The invention relates to a process for producing a custom-made hot moldable semi-finished product, in which at least two steel sheets of different grades of material quality and thickness are joined by laser welding in the top-to-end process. top, with at least one of the plates being produced from pressure-hardened steel and has a metallic coating based on aluminum or aluminium-silicon, and laser welding occurs with auxiliary wire feeding in the welding melt generated exclusively by means a laser beam, the auxiliary wire being substantially free of aluminum and at least one alloying element which favors the formation of austenite, which is present in the auxiliary wire in a passing proportion of at least 0.1% by weight as pressure hardenable steel, and the additional wire being heated prior to introduction into the welding melt by means of a heating device.
    [0002] Bespoke sheet steel plates (called Tailored Blanks) are used in automobile construction to meet high requirements for crash safety with the least possible body weight. For this purpose, individual plates or strips of different grades of material quality and/or plate thicknesses are joined by laser welding in the end-to-end process. In this way, different points of a bodywork component can be adapted to different loads. Thus, at points with a high load, thicker or also more solid steel sheets can be used, and at other points thinner sheets or sheets with relatively soft degrees of deep drawing are used. Through such bespoke sheet metal plates, additional reinforcement points on the bodywork become superfluous. This saves material and makes it possible to reduce the total weight of the body.
    [0003] In modern body construction, manganese-boron steels are used, which achieve high strengths, for example, extension strengths in the range of 1500 to 2000 MPa in hot molding with rapid cooling. In the initial stage manganese-boron steels typically have a ferritic-pearlite texture and have an extension strength of about 600 Mpa. By tempering under pressure, that is, by heating to austenitizing temperatures and then rapid cooling, a martensitic texture can be set, so that the steels thus treated can reach extension strengths in the range of 1500 to 2000 MPa.
    [0004] Among other corrosion protection reasons, steel sheets are coated with a metallic corrosion protection layer. Pressure hardenable steel sheet for the production of tailored blanks (tailored blanks) is normally provided with a metallic coating based on aluminium-silicon. In this case, metallic coating is composed of an inner layer of an intermetallic alloy and an outer layer of a metal alloy. However, the use of such coated steel sheets has considerable difficulties. This is because, when welding coated steel plates, a part of the AlSi coating reaches the molten mass generated at the junction and can form fragile intermetallic phases or ferritic zones, which are still present after the austenitization and sudden cooling of the plates. In these intermetallic or ferritic zones, failure or rupture of the weld seam can occur when a subsequent mechanical load is carried out under static or dynamic conditions. To prevent penetration of a part of the AlSi coating into the solder mass, it has already been proposed to remove a layer from the edge region of the board edges to be soldered, before soldering. This additional process step, however, is very expensive and time-consuming.
    [0005] In EP 2007545 B1 it is proposed to remove only the outer metal alloy layer before the AlSi coating, which can be worn relatively simply by brushing or by means of a laser jet. The much thinner, more difficult to remove intermetallic alloy layer is left on the steel plate to be welded. However, this partial coating removal is also costly and time-consuming. Furthermore, when welding thinned steel plates according to EP 2007545 B1 aluminum from the intermetallic alloy layer can reach the solder mass in such a quantity that a reduction in the hardening capacity of the solder seam has been observed.
    [0006] In addition, laser welding of bespoke blanks partially leads to a reduction in the cross section of the support plate. Due to the shear gap that arises when cutting the steel sheet to be welded, the occurrence of an outer layer and/or a relapse of the weld root partially results in the weld seam. This problem mainly exists in combinations of sheets with equal thickness and different grades of material quality. Unlike bespoke blanks for cold forming, the weld seam of bespoke blanks for hot forming does not show high strength to the steel sheet material after heat treatment in the furnace and after quenching. In the case of custom blanks for cold forming, this increase in strength can compensate for the influence of the cross-sectional area of the sheet. This is not possible in the case of bespoke blanks for conventional hot molding.
    [0007] From the document EP 1878531 B1 a hybrid laser-arc welding process is known, in which manganese-boron steel plates, which have a coating containing aluminum, are bonded together in the end-to-end process. The laser beam is combined with at least one electric arc to fuse the metal at the junction and weld the plates together. In this case, the arc is applied by means of a tungsten welding electrode or is formed when using MIG welding torches at the end of an auxiliary wire. The auxiliary wire may contain alloying elements (eg Mn and Ni) which favor an austenitic transformation of the welding wire texture and therefore favor the tempering capacity. With this hybrid welding process, it is achieved that hot moldable manganese-boron steel plates, which are provided with an aluminum-silicon-based coating, can be welded without prior removal of the coating material in the region of the welding wire. be produced, however, it must be ensured that the aluminum found at the joint edges of the plates does not lead to a reduction in the resistance to extension of the component at the weld seam. By providing an arc behind the laser beam, the solder mass is homogenized and thus local aluminum concentrations greater than 1.2% by weight, which generate a ferritic texture, are eliminated.
    [0008] The hybrid laser-arc arc welding process, however, is comparatively slow and expensive in relation to energy consumption due to the generation of the additional arc-flash. In addition, this process generates a very wide weld seam with excessive seam and root lift.
    [0009] Furthermore, it is known from document DE 102012111118 B3 which traces to the applicant a process for laser welding workpieces made of manganese-boron steel (MnB steel) with butt joint, in which the workpieces have a thickness of at least 1.8 mm and/or at the butt joint there is a difference in thickness of at least 0.4 mm, and in which laser welding occurs with the introduction of auxiliary wire n into the solder mass generated exclusively with a laser ray. To ensure that, when hot molding, the weld seam can safely harden into a martensitic texture, it is provided in this process that the auxiliary wire contains at least one alloying element from the group comprising manganese, chromium, molybdenum, silicon and/or nickel, which favors the formation of austenite in the loose mallet, and this alloy element is present with a higher percentage of mass in the auxiliary wire by at least 0.1% by weight than in the steel of the piece. work hardened under pressure. In this case, the workpieces may have an aluminum or aluminium-silicon metallic coated coating, which is removed at the edge along the edges to be welded, prior to laser welding. In addition, in this process, it is foreseen that the auxiliary wire is heated to a temperature of at least 50°C before being introduced into the solder mass for at least one longitudinal section. In practice, the process proved to be adequate. Removing the metallic coating on the edge of the steel sheets to be welded using laser radiation or mechanical grinding, however, is very expensive and time-consuming.
    [00010] The invention aims to provide a laser welding process, with which steel sheets of different grades of material quality and/or thickness, of which at least one sheet is made of hardenable steel under pressure and a Aluminum or aluminium-silicon based metallic coating, can be joined in the end-to-end process, whose weld seam can be transformed into a martensitic texture (for example, in an MnB-MnB compound) or a blend texture (for example, in a composite of MnB steel with microalloyed steel) when hot forming (pressure quenching), the welding process must be comparatively inexpensive and offer an optimized welding wire geometry.
    [00011] To achieve this goal, a process with the characteristics of the invention is proposed.
    [00012] The process according to the invention serves for the production of a bespoke hot molded sheet semi-finished product. In the process at least two steel sheets of different grades of material quality and/or thickness are joined end to end by laser welding, preferably manganese-boron steel is produced and has a metallic coating to the aluminum or aluminum base. -silicon. Laser welding occurs with the introduction of auxiliary wire into the solder mass generated exclusively by means of at least one laser beam, the auxiliary wire being substantially free of aluminum and containing at least one alloying element that favors the formation of austenite, which is present in the auxiliary wire in a proportion at least 0.1% by weight greater than in the pressure hardenable steel, and the auxiliary wire being heated by means of a heating device before introduction into the solder mass. the process according to the invention is further characterized by the fact that the steel sheets are welded together with a clearance limited by their edges to be welded together, which has an average width of at least 0.15mm , whereby so much auxiliary wire material is introduced into the slit, that the ratio of auxiliary wire volume introduced into the slit to the volume of molten steel sheet material by means of said at least one laser beam is at least 20%, preferably at least 30%.
    [00013] By "aluminum-free or substantially aluminum-free auxiliary wire", in the context of the invention, it is meant an auxiliary wire that does not contain aluminum except unavoidable impurities or unavoidable small percentages.
    [00014] In the laser welding process according to the invention, it is neither necessary nor foreseen to previously rough out the edge of a steel plate that has a metallic coating based on aluminum or aluminum-boron. By virtue of the absence of roughing on the edge side (grinding) of the metallic coating, the process according to the invention is markedly shorter than the process known according to EP 2007545 B1.
    [00015] As the steel sheets are joined, according to the invention, with a slot that has an average width of at least 0.15mm, preferably of at least 0.18mm, more preferably of at least 0.2mm, being that the diameter of the laser beam or the width of the laser beam at the point of incidence on the joint remains substantially unchanged compared to the usual laser beam diameter, it is guaranteed that less material of the steel sheets and, consequently, less volume of the coating containing aluminum is melted and penetrates the solder mass. Furthermore, the introduction of the auxiliary wire leads to a better homogenization of the solder mass, that is, the volume of aluminum that penetrates into the molten mass from the metallic coating is considerably reduced and is distributed very evenly or almost homogeneously. According to the invention, so much of the auxiliary wire material is inserted into the slit, that the ratio of the auxiliary wire volume introduced into the slit to the volume of the steel sheet material cast by means of the laser beam is at least 20% or at least minus 30%, preferably 35%, more preferably 40%.
    [00016] The average slit width should not be set by more than 0.5mm. Therefore, the method according to the invention can be carried out with conventional laser beam welding optics, since the diameter or width of the laser beam at the point of incidence on the joint must remain as unchanged as possible. A smaller average gap width and welding exclusively using laser radiation enable a narrow weld seam with little excessive seam or root lift compared to the relatively wide weld seam in hybrid laser-flash welding. For the same reasons, the volume ratio of auxiliary wire introduced into the slit to the volume of the molten steel sheet material by means of said at least one laser beam should not be greater than 60%.
    [00017] The auxiliary wire used in the process according to the invention is substantially free of aluminum and contains at least one alloying element that favors the formation of austenite, which is present in the auxiliary wire with a pass percentage of at least 0. 1% by weight, preferably at least 0.2% by weight greater than pressure hardenable steel. By providing one or more alloying elements that favor the formation of austenite, the hardening capacity of the weld seam is improved. Preferably the auxiliary wire contains at least manganese and/or nickel as alloying elements which favor the formation of austenite or stabilize the austenite.
    [00018] Another preferred configuration of the process according to the invention provides that the auxiliary yarn used has the following composition: 0.05 to 0.15% by weight of C, 0.5 to 2.0% by weight of Si, 1.0 to 3.0% by weight of Mn, 0.5 to 2.00% by weight of Cr+Mo, and 1.0 to 4.0% by weight of Ni, the rest of Fe and unavoidable impurities. Internal experiments have resulted in that, with such an auxiliary wire and the use of the process according to the invention, a complete conversion of the weld seam into a martensitic texture (for example, for MnB-bonding can be guaranteed with great confidence). MnB) or a mixed texture (eg MnB steel bond with microalloyed steel) when the next hot molding (pressure quenching) of the custom blanks.
    [00019] According to another preferred embodiment of the process according to the invention, the auxiliary wire employed therein has a carbon mass ratio at least 0.1% by weight lower than that of steel hardenable under pressure of at least one of the plates to be welded together. This prevents the weld seam from weakening. In particular, a good possibility of good residual rotation of the weld seam can be achieved through the relatively low carbon content of the auxiliary thread.
    [00020] According to the invention, the auxiliary wire is heated before introducing it into the solder mass by means of a heating device. For example, the auxiliary yarn is heated to a temperature of at least 60°C, preferably at least 100°C, more preferably at least 150°C prior to introduction into the melt by means of a heating device. This makes a significantly higher welding speed possible compared to an unheated auxiliary wire. This is because the tip of the heated auxiliary wire can be fused more quickly with the laser beam. Furthermore, the welding process is made more stable by heating the auxiliary wire before introducing it into the solder mass.
    [00021] The welding speed or the speed with which the steel sheets to be welded together end to end are moved in relation to the laser beam, in the process according to the invention, is at least 3 m/min, preferably at least 6 m/min, more preferably at least 9 m/min.
    [00022] To heat the auxiliary wire quickly and efficiently, in the process according to the invention, a heating device is preferably used that heats the auxiliary wire inductively, electrically, conductively or through heat radiation before introduction into the mass of solder. The electrical heating of the auxiliary wire preferably takes place in such a way that an electrical current is conducted in contacts through the auxiliary wire. The speed at which the auxiliary wire is fed is preferably in the range from 70 to 100% of the laser welding speed.
    [00023] Compared to laser beam welding after pre-roughing the edges of coated steel sheets to be butt welded, the process according to the invention achieves an optimized weld seam geometry, namely a cross section of larger support plate edge. This is especially advantageous for dynamic later loads of the weld seam.
    [00024] A manganese-boron steel is used in preference to a pressure hardenable steel. In a preferred embodiment of the process according to the invention, at least one of the steel sheets to be butt-welded together is chosen in such a way that it has a hardenable steel of the following composition: 0.10 - 0.50 % by weight of C, max. 0.40% by weight of Si, 0.50 - 2.00% by weight of MN, max. 0.025% by weight of P, max. 0.010% by weight of S, max. 0.60% by weight of CR, max. 0.50% by weight of Mo, max. 0.050% by weight Ti, 0.0008 - 0.0070% by weight B, and min. 0010% by weight of Al. The rest of Fe and unavoidable impurities. Components made of such sheet steel have a high resistance to extension after hardening under pressure. Sheets of different or identical manganese-boron steels can be welded also with the process according to the invention, to provide tailor-made semi-finished sheet products which exhibit maximized strengths through a pressure quenching.
    [00025] Another advantageous configuration of the process according to the invention is characterized by the fact that at least one of the steel sheets is not hardenable under pressure and, for example, is made of microalloyed steel. By combining a pressure hardenable steel sheet, such as manganese-boron steel, with a microalloyed steel sheet, a distinctive stretch strength or ductility can be locally set in a bodywork component, eg B column. In this case, the microalloyed steel preferably has the following composition: 0.05 - 0.15% by weight of C, max. 0.50% by weight Si, 0.40 - 1.20% by weight Mn, max. 0.030% by weight of P, max. 0.025% by weight of S, 0.01 - 0.12% by weight of Nb, 0.02 - 0.18% by weight of Ti, 0.0008 - 0.0070% by weight of B, and at least 0.010 % by weight of Al, the rest of Fe and unavoidable impurities. Such steel is distinguished by an A80 breaking elongation of at least 21%.
    [00026] The steel sheets used in the process according to the invention have, including the metallic coating, a sheet thickness in the preferable range of 0.6 to 3.0 mm.
    [00027] According to another advantageous configuration of the process according to the invention, said at least one laser beam is a focus beam of lines that is directed towards the edges of the steel sheets to be welded together in such a way, that the longitudinal axis of the line focus ray incident on the edges passes substantially parallel to the edges. Through the focus of lines, the soldering mass remains liquid longer before it hardens. This also contributes to a better mixing (homogenization) of the solder mass. the focus length of lines can be, for example, in the range of 1.2 to 2.0 mm.
    [00028] To prevent a weakening of the weld seam, another configuration of the process according to the invention provides that the weld mass is required during laser welding with shielding gas (inert gas). In this case, preferably pure argon, helium, nitrogen or a mixture of argon, helium, nitrogen and/or carbon dioxide and/or hydrogen is used as the shielding gas.
    [00029] The invention is clarified below in more detail with the aid of a drawing representing embodiment examples. They are shown schematically:
    [00030] Figure 1 - a perspective representation of parts of a device for carrying out the laser welding process according to the invention, with two steel plates of equal thickness, which differ from each other in the sense of their degree of material quality, they are welded together end to end;
    [00031] Figure 2 - a cross-sectional view of a section of the steel plates welded together from figure 1;
    [00032] Figure 3 - a perspective representation of parts of a device for carrying out the laser welding process according to the invention, here two plates of different thicknesses with different degrees of material quality are welded together; and
    [00033] Figure 4 - a cross-sectional view of the section of the steel plates welded together in figure 3.
    [00034] Figure 1 schematically shows parts of a laser welding device, with which the laser welding process according to the invention can be carried out. The device comprises a displaceable base or support plate (not shown), on which two steel plates 1, 2 of different grades of material quality are disposed. One sheet 1, 2 is made of pressure hardenable steel, preferably manganese-boron steel, while the other sheet 2 or 1 is made of a relatively soft, deep drawing quality grade, preferably of microalloyed steel.
    [00035] The pressure hardenable steel can have, for example, the following chemical composition: Max. 0.4% by weight of C, Max. 0.4% by weight of Si, max. 2.0% by weight Mn, Max. 0.025% by weight P, Max. 0.010% by weight S, Max. 0.8% by weight Cr+Mo, Max. 0.05% by weight Ti , Max. 0.007% by weight of B, and Min. 0.015% by weight of Al,
    [00036] The rest of Fe and unavoidable impurities.
    [00037] In the state of delivery, that is, before heat treatment and rapid cooling, the yield strength Re of the pressure hardenable steel sheet 1 or 2 is preferably at least 300 MPa, its resistance to extension is at least minus 480 MPa, and its A80 breakout elongation is in the range of 10 to 15%. After hot molding (pressure quenching), that is, heating to an austenitizing temperature of about 900 to 920°C and subsequent rapid cooling, this steel sheet 1 or 2 has a yield strength Re of about 1,100 MPa, an extension strength Rm of about 1500 to 2000 MPa and an elongation at break A80 of about 5%.
    [00038] Sheet 2 or 1 steel with relatively soft deep drawing degree or microalloyed steel preferably has the following chemical composition: Max. 0.1% by weight of C, Max. 0.35% by weight of Si, Max. 1.0% by weight Mn, Max. 0.030% by weight P, Max. 0.025% by weight S, Max. 0.10% by weight Nb, Max. 0.15% by weight Ti , Max. 0.007% by weight of B, and Min. 0.015% by weight of Al,
    [00039] The rest of Fe and unavoidable impurities.
    [00040] At least one of the sheets 1, 2 has a metallic coating 1.1, 2.1 based on aluminum or aluminium-silicon. In the example sketched in figure 1 both plates 1, 2 are provided with such a coating 1.1, 2.1. Coating 1.1, 2.1 can be applied over a steel strip typically through a continuous melt-dip coating process, from which the sheets 1, 2 are obtained by cutting.
    [00041] The plates 1, 2 shown in figure 1 have substantially the same thickness. The thickness of sheets 1, 2 including coating 1.1, 2.1 is, for example, in the range of 0.6 to 3.0mm. The thickness of the coating 1.1, 2.1 on the respective upper or lower side of the sheet 1, 2 is, for example, in the range of about 10 to 120 µm and preferably is less than or equal to 50 µm.
    [00042] Above plate 1, 2 is sketched a portion of a laser welding head 3, which is provided with an optic (not shown) for feeding a laser beam 4, as well as a focusing device for bundling a laser beam 4. Furthermore, on the laser welding head 3 a line 5 for supplying shielding gas is arranged. The opening of the shielding gas line 5 is substantially directed towards the region of focus of the laser beam 4 or towards the solder mass 6 generated by means of the laser beam 4. As shielding gas, for example argon or a mixture is used. of argon with helium and/or carbon dioxide.
    [00043] Furthermore, the laser welding head 3 is associated with a wire feed device 7, by means of which a special additional material in the form of a wire 8 is fed to the welding mass 6, which is also melted by means of laser beam 4. The weld seam is designated 9. The additional wire 8 is substantially free of aluminum and contains at least one alloying element which favors the formation of austenite or stabilizes the austenite, preferably manganese and/or nickel.
    [00044] The plates or plates 1,2 are joined end to end with a slit G, the width of which is at least 0.15 mm, preferably at least 0.2 mm. The average width b of the gap G that limits the sheet edges to be welded together is in the range of 0.15 to 0.5mm. Coating 1.1, 2.1 of aluminum or aluminium-silicon extends, on coated steel sheet 1 and/or 2, to the sheet edges to be butt welded. The welding of plates 1, 2 takes place, therefore, without roughing (prior) the edge of the edges to be welded.
    [00045] The focusing device bundles the laser beam 4 into a focus substantially in the shape of a point or circle, or preferably into a focus of lines. The diameter or width of the laser beam 4 at the point of incidence on plates 1, 2 is in the range of about 0.7 to 0.9mm. Through the relatively wide gap G, whose width b is at least 0.15mm and can be, for example, in the range of 0.25 to 0.5mm, it is guaranteed that less material from plates 1, 2 and, consequently, also less volume of the coating 1.1, 2.1 containing aluminum is melted and flows into the melt 6. Slot G is filled with the molten material from the auxiliary river 8, which has, in the solid state, a diameter in the range of about 0 .8 to 1.2 mm. The introduction of the auxiliary wire material into the gap G leads to considerable thinning as well as homogeneous distribution of the aluminum flowing from the molten edge of the coating 1.1, 2.1 to the molten mass 6. The volume ratio of auxiliary river introduced into the gap G for the volume of the steel sheet material cast by means of the laser beam 4 is at least 20% and is preferably in the range of 30 to 60%.
    [00046] The auxiliary yarn 8 has, for example, the following chemical composition: 0.1% by weight of C, 0.9% by weight of Si, 2.2% by weight of Mn, 0.4% by weight of Cr, 0.6% by weight of Mo, and 2.2% by weight of Ni,
    [00047] The rest of Fe and unavoidable impurities.
    [00048] The manganese content of the auxiliary wire 8 in this case is greater than the manganese content of the pressure hardenable steel sheet. Preferably the manganese content of the auxiliary wire 8 is at least 0.2% by weight greater than the manganese content of the pressure hardenable steel sheet. It is also advantageous that the chromium and molybdenum content of the auxiliary wire 8 is greater than in the pressure hardenable steel sheet 1 or 2. Preferably the combined chromium-molybdenum content of the auxiliary wire 8 is at least 0.1% in weight greater than the combined chromium-molybdenum content of the pressure hardenable steel sheet 1 or 2. The nickel content of the auxiliary wire 8 is preferably in the range of 1.0 to 4.0% by weight, especially in the range of 2.0 to 2.4% by weight. Furthermore, the auxiliary wire 8 preferably has a lower carbon content than the pressure hardenable steel sheet 1 or 2. The carbon content of the auxiliary yarn 8 is preferably in the range of 0.05 to 0.15% by weight.
    [00049] The auxiliary wire 8 is fed in a heated state in the molten mass generated through the laser beam 4. For this the wire feeding device 7 is equipped with a heating device (not shown), which heats the auxiliary wire. 8 preferably inductively, electrically, conductively or through heat radiation. The length of auxiliary yarn 8 thus heated has a temperature of, for example, 60°C, preferably at least 150°C, more preferably at least 180°C.
    [00050] The laser source of the laser welding device is, for example, a CO2 laser, diode laser or filament laser, in the sense of layer type. The laser source provides, during the welding process, an extension energy of at least 0.3 kJ/cm at a laser power of at least 7 kW. The welding speed is, for example, in the range of 3 to 9 m/min or preferably above 8 m/min. The auxiliary wire 8 is fed with a speed that is in the range of 70 to 100% of the laser welding speed.
    [00051] The embodiment shown in Figures 3 and 4 differs from the embodiment shown in Figures 1 and 2 by the fact that the steel sheets 1, 2' have different thickness, so that, at the top joint, a difference in thickness d of at least 0.2 mm results. For example, the pressure curable steel sheet 1 has a sheet thickness in the range of 0.5 mm to 1.2 mm, while the sheet 2' of microalloyed steel or relatively ductile steel has a sheet thickness in the range of 1.4mm to 3.0mm.
    权利要求:
    Claims (14)
    [0001]
    1. Process for producing a bespoke hot moldable sheet semi-finished product in which at least two steel sheets (1, 2, 2') of different grades of material quality and/or thickness are joined end-to-end through of laser welding, at least one of the steel sheets (1, 2, 2') being made of hardened steel under pressure and having a metallic coating (1.1, 2.1) based on aluminum or aluminium-silicon. the laser welding takes place by feeding auxiliary wire (8) to the molten mass (6) generated exclusively by means of at least one laser beam (4), the auxiliary wire (8) being substantially free of aluminum and containing at least an alloying element that favors the formation of austenite, which is present in the auxiliary wire (8) with a percentage by mass at least 0.1% by weight greater than in the pressure-curable steel, and the auxiliary wire ( 8) is heated before feeding to the welding mass (6) by means of a heating device tion, characterized by the fact that the steel plates (1, 2, 2') are welded together so that there is a gap (G), which is limited by the edges of the plates to be welded together, where the steel plates (1,2.2') are positioned in such a way that the slot (G) limited by the edges of the plates to be welded together has an average width (b) in the range of 0.15 to 0 .5 mm, and the amount of auxiliary wire (8) material that is introduced into the slot (G) is such that the ratio of auxiliary wire volume introduced into the slot (G) to the volume of steel sheet material cast by means of laser beam (4) is in the range of 30 to 60%.
    [0002]
    2. Process according to claim 1, characterized in that the auxiliary wire (8) is heated prior to introduction into the melt (6) by means of a heating device in an inductive, electrical, conductive or radiation manner of heat.
    [0003]
    3. Process according to claim 1 or 2, characterized in that the auxiliary wire (8) is heated prior to introduction into the melt (6) by means of the heating device to a temperature of at least 100°C.
    [0004]
    4. Process according to any one of claims 1 to 3, characterized in that the pressure curable steel is a manganese-boron steel.
    [0005]
    5. Process according to any one of claims 1 to 4, characterized in that the pressure curable steel has the following composition: 0.10 - 0.50% by weight of C, max. 0.40% by weight of Si, 0.50 to 2.0% by weight of Mn, max. 0.025% by weight of P, max. 0.010% by weight of S, max. 0.60% by weight of Cr, max. 0.50% by weight of Mo, max. 0.050% by weight T, 0.0008 - 0.0070% by weight B, and min. 0.010% by weight of Al, the rest of Fe and unavoidable purities.
    [0006]
    6. Process according to any one of claims 1 to 5, characterized in that at least one of the steel sheets (1, 2, 2’) is made of microalloyed steel.
    [0007]
    7. Process according to claim 6, characterized in that the microalloyed steel has the following composition: 0.05 - 0.15% by weight of C, max. 0.35% by weight Si, 0.40 - 1.20% by weight Mn, max. 0.030% by weight of P, max. 0.025% by weight of S, 0.01 - 0.12% by weight of Nb, 0.02 - to 0.18% by weight of Ti, 0.0008 - 0.0070% by weight of B, and min. 0.010% by weight of Al, the rest of Fe and unavoidable purities.
    [0008]
    8. Process according to any one of claims 1 to 7, characterized in that said at least one laser beam (4) in the form of a line focus ray is directed to the edges of the steel plate (1, 2, 2') to be welded together, in such a way that the longitudinal axis of the line focus ray incident on the edges passes substantially parallel to the edges.
    [0009]
    9. Process according to any one of claims 1 to 8, characterized in that the auxiliary wire (8) contains at least manganese and/or nickel as alloying elements that favor the formation of austenite.
    [0010]
    10. Process according to any one of claims 1 to 9, characterized in that the auxiliary yarn (8) has the following composition: 0.05 - 0.15% by weight of C, 0.5 - 2.0 % by weight of Si, 1.0 - 3.0% by weight of Mn, 0.5 - 2.0% by weight of Cr+ Mo, and 1.0 - 4.0% by weight of Ni, the rest of Fe and unavoidable impurities.
    [0011]
    11. Process according to any one of claims 1 to 10, characterized by the fact that the auxiliary wire (8) has at least 0.1% by weight lower percentage of carbon than pressure curable steel.
    [0012]
    12. Process according to any one of claims 1 to 11, characterized in that the auxiliary wire (8) is fed at a speed ranging from 70 to 100% of the laser welding speed.
    [0013]
    13. Process according to any one of claims 1 to 12, characterized in that the molten mass (6) is requested with shielding gas during laser welding.
    [0014]
    14. Process according to claim 13, characterized in that as shielding gas pure argon or a mixture of argon and carbon dioxide is used.
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    同族专利:
    公开号 | 公开日
    WO2017050711A1|2017-03-30|
    EP3352940A1|2018-08-01|
    PT3352940T|2022-01-19|
    KR20190026985A|2019-03-13|
    BR112018002126A2|2018-09-11|
    KR101999820B1|2019-07-12|
    US10543565B2|2020-01-28|
    CN108025400B|2020-08-04|
    US20180326538A1|2018-11-15|
    RU2680485C1|2019-02-21|
    ZA201800658B|2019-06-26|
    CA2999105A1|2017-03-30|
    DE102015115915A1|2017-03-23|
    EP3352940B1|2021-12-15|
    MX2018001700A|2018-05-07|
    KR20180033593A|2018-04-03|
    CN108025400A|2018-05-11|
    JP2018534143A|2018-11-22|
    JP6430070B2|2018-11-28|
    CA2999105C|2020-04-14|
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    法律状态:
    2020-02-27| B06U| Preliminary requirement: requests with searches performed by other patent offices: procedure suspended [chapter 6.21 patent gazette]|
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    2021-08-17| B16A| Patent or certificate of addition of invention granted [chapter 16.1 patent gazette]|Free format text: PRAZO DE VALIDADE: 20 (VINTE) ANOS CONTADOS A PARTIR DE 20/09/2016, OBSERVADAS AS CONDICOES LEGAIS. |
    优先权:
    申请号 | 申请日 | 专利标题
    DE102015115915.5|2015-09-21|
    DE102015115915.5A|DE102015115915A1|2015-09-21|2015-09-21|Laser welding process for the production of a semi-finished sheet of hardenable steel with an aluminum or aluminum-silicon based coating|
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