Classifications

• • B—PERFORMING OPERATIONS; TRANSPORTING
  • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
  • B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
  • B23K20/00—Non-electric welding by applying impact or other pressure, with or without the application of heat, e.g. cladding or plating
  • B23K20/12—Non-electric welding by applying impact or other pressure, with or without the application of heat, e.g. cladding or plating the heat being generated by friction; Friction welding
• • C—CHEMISTRY; METALLURGY
  • C21—METALLURGY OF IRON
  • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
  • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
  • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
• • C—CHEMISTRY; METALLURGY
  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22C—ALLOYS
  • C22C38/00—Ferrous alloys, e.g. steel alloys
• • C—CHEMISTRY; METALLURGY
  • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
  • C22C—ALLOYS
  • C22C38/00—Ferrous alloys, e.g. steel alloys
  • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium

Definitions

• the present invention relates to a solid phase bonding method for steel materials and a solid phase bonded joint obtained by the solid phase bonding method.
• the solid-phase joining method which can reduce the decrease in strength of the joint compared to conventional fusion welding, is attracting attention, and in particular, solid-phase joining methods that utilize the phenomenon of frictional heat generation and plastic deformation of metal materials are being actively studied.
• the solid phase welding method include friction stir welding (FSW), in which a columnar tool rotating at high speed is pressed into the workpiece to join the workpiece,
• FSW friction stir welding
• Examples include “friction welding” in which the material is brought into contact with the material to be bonded and “linear friction welding” in which the material to be bonded is reciprocated while being in contact with the material to be bonded.
• the deformation resistance of the steel in friction stir welding is increased by expanding the ferrite single-phase region and the austenite phase-ferrite two-phase region near the ultimate temperature of the joint.
• the durability of the rotating tool is improved, and restrictions on welding conditions such as welding speed are relaxed.
• the frequency of replacement work due to tool wear and damage is suppressed, and the welding time is shortened, improving construction efficiency.
• Patent Document 2 Japanese Patent Application Laid-Open No. 2018-16866
• the steel composition, in mass% is C: 0.20 to 0.45% and Cr: 1.00 to 3.50.
• the carbon equivalent CE defined by the formula A is 0.40 to 1.00% by mass.
• CE C + Mn / 6 + (Cu + Ni) / 15 + (Cr + Mo + V) / 5 (A)
• the element symbols described in the formula indicate the content of each component in the friction stir welding steel material in units of mass%.
• the steel for friction stir welding described in Patent Document 2 is a steel that can obtain joint properties (such as tensile strength and fracture toughness of the stir zone) equivalent to or higher than those of conventional high-strength steel by friction stir welding, It states that it is possible to provide a relatively inexpensive steel to which only alloying elements are minimally added, and a friction stir welding method using the steel as a material to be welded.
• Patent Document 1 facilitates the application of friction stir welding to steel by reducing the deformation resistance of the steel during the process, and the mechanical properties of the joint and reliability are not considered.
• an object of the present invention is to provide a solid phase bonding method that simply and efficiently suppresses the softening of the heat affected zone when a steel material is used as the material to be welded, and the solid phase bonding method.
• An object of the present invention is to provide a solid phase welded joint in which softening of the heat-affected zone obtained by the method is suppressed.
• the present inventors have extensively studied the relationship between the composition of steel and the conditions for solid phase joining. It was found that it is an area where More specifically, the softening at the solid-phase joint occurs due to the precipitation of carbides from martensite, and the higher the temperature, the more pronounced the softening. Therefore, the degree of softening decreases. In contrast, the present inventors have found that softening in the heat-affected zone can be effectively suppressed by setting the A1 point temperature to a temperature at which secondary hardening of the steel occurs, and the like, and have arrived at the present invention.
• the present invention A solid phase bonding method in which at least one of the materials to be bonded is made of steel,
• the steel material has an additive element that develops secondary hardening, forming a region in which the highest temperature reached by the steel material during joining is the A1 point temperature of the steel material,
• the A 1 point temperature is the temperature at which the secondary curing is expressed,
• Solid phase bonding method used in the present invention is not particularly limited as long as it does not impair the effects of the present invention, and various conventionally known solid phase bonding methods can be used.
• Solid phase welding methods include friction welding such as friction stir welding, friction welding and linear friction welding, pressure welding, explosive welding, ultrasonic welding and diffusion welding. Stir welding, friction welding, and linear friction welding are preferably used, and friction stir welding, which can also be applied to the joining of large members, is more preferably used.
• the A1 point temperature of the steel material may be experimentally measured by a transformation point measurement test or the like, or may be determined from the composition using commercially available thermodynamic calculation software. Also, if there is a database of A1 point temperature corresponding to the composition of the steel material, the value may be used.
• the additive element that exhibits secondary hardening is not particularly limited as long as it does not impair the effects of the present invention, and conventionally known various additive elements that cause secondary hardening of steel can be used. is preferred. Steel containing V exhibits significant secondary hardening due to the precipitation of fine VC, so softening in the heat affected zone can be effectively suppressed.
• the A1 point temperature of the steel material is preferably 400 to 650°C, more preferably 575 to 625°C.
• the A1 point temperature of the steel material is preferably 400 to 650°C, more preferably 575 to 625°C.
• the A1 point temperature is controlled by the amount of Mn added to the steel material.
• the A1 point temperature of the steel material is determined by the composition, but by controlling the amount of Mn added, the A1 point temperature can be easily and efficiently arbitrarily set.
• the Vickers hardness difference between the most softened region and the base material based on the martensite structure is 100 HV or less.
• the Vickers hardness difference between the most softened region and the base material is more preferably 75 HV or less, most preferably 50 HV or less.
• the Vickers hardness of the softened region is 450 HV or more.
• the Vickers hardness of the most softened region is more preferably 500 HV or higher, most preferably 550 HV or higher.
• At least one of the materials to be joined is a steel material
• the steel material has an additive element that develops secondary hardening
• the A1 point temperature of the steel material is 400 to 650 ° C.
• the Vickers hardness difference between the most softened region and the base material is 100 HV or less
• a solid state bonded joint characterized by:
• V, W and Mo are preferable as additive elements for developing secondary hardening, and V is more preferable. Since the steel contains these elements, the softening of the most softened region is suppressed by fine precipitates.
• the solid phase bonded joint of the present invention can be suitably obtained by the solid phase bonding method of the present invention, and the Vickers hardness difference between the most softened region and the base material is 100 HV or less. It is a fully utilized solid phase joint joint.
• the Vickers hardness difference between the most softened region and the base material is more preferably 75 HV or less, most preferably 50 HV or less.
• the Vickers hardness of the softest region is 450 HV or more. Since the Vickers hardness of the most softened region is 450 HV or more, even when ultra-high-strength steel is used as the material to be welded, a solid phase welded joint that fully utilizes the mechanical properties of the material to be welded. can do.
• the Vickers hardness of the most softened region is more preferably 500 HV or higher, most preferably 550 HV or higher.
• the solid-phase welded joint of the present invention has a friction stir weld.
• the solid phase joint in the solid phase welded joint of the present invention is not particularly limited as long as it does not impair the effects of the present invention, and various conventionally known solid phase joints can be used. can form a solid phase joint in any region.
• a solid phase bonding method for simply and efficiently suppressing the softening of the heat affected zone when a steel material is used as the material to be joined, and the softening of the heat affected zone obtained by the solid phase joining method is suppressed. It is possible to provide a solid state bonded joint.
• FIG. 3 is a schematic diagram showing a cross-sectional macrostructure of a joint obtained by friction stir welding.
• FIG. 3 is a schematic diagram showing a cross-sectional macrostructure of a joint obtained by linear friction welding.
• FIG. 2 is a schematic diagram showing a cross-sectional macrostructure of a joint obtained by linear friction welding.
• 1 is a schematic diagram of a solid phase welded joint obtained by friction stir welding;
• FIG. 2 is a schematic diagram of a solid phase welded joint obtained by linear friction welding; It is the hardness distribution of the cross section orthogonal to the joint part of the obtained joint (comparative steel plate 1). It is the hardness distribution of the cross section perpendicular to the joint portion of the obtained joint (comparative steel plate 2).
• FIG. 4 is an STEM observation image of the heat-affected zone of Comparative Steel Plate 1.
• FIG. 4 is an STEM observation image of the heat-affected zone of comparative steel plate 2.
• FIG. 11 shows the results of 3D-APT elemental distribution measurement within laths of the martensitic structure of FIG. It is the result of 3D-APT element distribution measurement in the maximum softening region of comparative steel plate 3. This is the result of 3D-APT elemental distribution measurement in the region where the highest temperature reached during joining was 600° C. in comparative steel plate 3.
• Friction Stir Welding Friction stir welding
• two metal members are joined by inserting a protruding portion (probe) between both ends and rotating and moving a rotating tool along the longitudinal direction of these ends.
• Friction stir welding includes (1) welding in which the ends of metal plates are butted together to form a joint, and a rotating tool is rotated and moved along the longitudinal direction of the processed portion to join the metal plates together; ) spot welding in which the ends of the metal plates are butted against each other to form a joint, and the rotary tool is rotated at the joint without moving it to join them; (3) the metal plates are overlapped at the joint and rotated to the joint Spot welding where metal plates are joined by inserting a tool and rotating the rotating tool without moving it at that point, (4) metal plates are superimposed at the joint, inserting the rotating tool into the joint, and rotating
• the four aspects (1) to (4) of joining metal plates by moving the tool while rotating it along the longitudinal direction of the joining part and combinations thereof are included, but the following are typical As a mode, "(1) bonding in which the ends of metal plates are butted together to form a joint, and the rotary tool is rotated and moved along the longitudinal direction of the processed portion to join the metal plates together" will be described in detail. do. The
• FIG. 1 schematically shows the macrostructure of the cross section of the joint obtained by friction stir welding (the cross section perpendicular to the welding line).
• the lower part of FIG. 1 also schematically shows the hardness distribution corresponding to the cross-sectional macrostructure.
• the hardness distribution is the hardness distribution along the dashed-dotted line of the cross section.
• a friction stir welded joint 2 is formed with a friction stir portion 4 , a heat affected zone 6 is present on the outer edge of the friction stir welded portion 4 , and a base material portion 8 is formed outside the heat affected zone 6 .
• the hardness of the friction stir zone 4 varies depending on the type of steel material to be welded and friction stir welding conditions, and there are cases where it is lower than that of the base material part 8 and cases where it is higher. Lower than the material portion 8 . In particular, the decrease in the hardness of the heat affected zone 6 becomes significant when the hardness of the steel material is high (when the strength is high).
• the softened region in the friction stir welded joint 2 is the heat affected zone 6, where the highest temperature reached during welding is It became clear that it is the area
• steel materials having an additive element that exhibits secondary hardening are used as the materials to be joined, and the A1 point temperature of the steel material is set to the temperature at which secondary hardening occurs, so that the heat effect The softening in the portion 6 can be effectively suppressed.
• the A1 point temperature of the steel material to be joined may be experimentally measured by a transformation point measurement test or the like, or may be determined from the composition using commercially available thermodynamic calculation software. Also, if there is a database of A1 point temperature corresponding to the composition of the steel material, the value may be used.
• the additive element that exhibits secondary hardening is not particularly limited as long as it does not impair the effects of the present invention, and conventionally known various additive elements that cause secondary hardening of steel can be used. is preferred. Steel containing V exhibits significant secondary hardening due to the precipitation of fine VC, so softening in the heat affected zone can be effectively suppressed.
• the A1 point temperature of the steel material is preferably 400 to 650°C, more preferably 575 to 625°C.
• the A1 point temperature of the steel material is preferably 400 to 650°C, more preferably 575 to 625°C.
• W and Mo as additional elements other than V.
• V, W and Mo have a moderate tendency to form carbides and are effectively Secondary carbides are generated in the region, and the decrease in hardness of the region can be suppressed extremely effectively.
• the generally known tendencies of forming carbides of alloying elements are Ti>Ta>Nb>V>W>Mo>Cr>Mn>(Fe)>Ni, Co, Al, Si. Since Ti, Ta, and Nb have too strong a tendency to form carbides, for example, they easily form carbides even in austenite, and the amount of secondary carbides formed in the heat affected zone 6 is reduced. can not be post-cured. On the other hand, Cr and Mn have too weak a tendency to form carbides, and the hardness of the carbides is relatively low, so that the heat affected zone 6 cannot be effectively secondary hardened.
• the A1 point temperature of the steel material is preferably controlled by the amount of Mn added.
• the A1 point temperature of the steel material is determined by the composition, but by controlling the amount of Mn added, the A1 point temperature can be set easily and effectively.
• the Mn content is preferably 3.0 to 5.0% by mass, and when emphasizing ductility, it is 2.00% by mass or more. It is preferably less than 0.00% by mass.
• the A 1 point temperature of 0.2C-3Mn-2Si-1V-Fe is 734 ° C.
• the A 1 point temperature of 0.2C-3.6Mn-2Si-1V-Fe is 625 ° C.
• 0 .2C-4Mn-2Si-1V-Fe A 1- point temperature is 572 ° C.
• 0.2C-4.4Mn-2Si-1V-Fe A 1- point temperature is 498 ° C.
• the A1 point temperature of -Fe is 380°C.
• the Vickers hardness difference between the most softened region in the heat affected zone 6 and the base material part 8 is preferably 100 HV or less. By setting the Vickers hardness difference between the most softened region and the base material portion 8 to 100 HV or less, a solid phase welded joint that fully utilizes the mechanical properties of the base material portion 8 can be obtained.
• the Vickers hardness difference between the most softened region and the base material portion 8 is more preferably 75 HV or less, most preferably 50 HV or less.
• the Vickers hardness of the most softened region in the heat affected zone 6 is 450 HV or more.
• the friction stir welded joint 2 can be provided with a tensile strength equal to or greater than that of ultra-high-strength steel.
• the Vickers hardness of the most softened region is more preferably 500 HV or higher, most preferably 550 HV or higher.
• the maximum softening region in the heat affected zone 6 (the region where the highest temperature reached during welding is the A1 point temperature of the steel material) can be controlled by the friction stir welding conditions. Specifically, the temperature of the friction stirrer 4 increases due to an increase in the rotation speed of the rotating tool, an increase in the applied pressure (bonding pressure), a decrease in the moving speed, etc., and the most softened region shifts to the base material 8 side. do. On the other hand, the temperature of the friction stirrer 4 decreases due to a decrease in rotational speed of the rotating tool, a decrease in applied pressure (bonding pressure), an increase in moving speed, etc., and the softened region shifts to the friction stirrer 4 side. Further, by setting the maximum temperature reached in the friction stir zone 4 to be equal to or higher than the A1 point temperature of the steel material, a region is formed in which the maximum temperature reached in the heat affected zone 6 is the A1 point temperature of the steel material.
• Linear friction welding is a solid phase welding method in which the materials to be welded are linearly slid to join.
• first step of forming an interface one member to be joined and the other member to be joined are repeatedly slid on the same trajectory while pressure is applied substantially perpendicularly to the interface to be joined, and sliding is performed. It has a second step of discharging burrs from the interface to be joined substantially parallel and substantially perpendicular to the direction, and a third step of stopping sliding to form a joint surface.
• Fig. 2 schematically shows the macrostructure of the cross section of the joint (the cross section perpendicular to the joint line) obtained by linear friction welding.
• the lower portion of FIG. 2 also schematically shows the hardness distribution corresponding to the cross-sectional macrostructure.
• the hardness distribution is the hardness distribution along the dashed-dotted line of the cross section.
• a joint interface 12 is formed in the linear friction-bonded joint 10 , a heat-affected zone 6 exists on the outer edge of the joint interface 12 , and a base material portion 8 is formed outside the heat-affected zone 6 .
• the hardness in the vicinity of the joint interface 12 changes depending on the type of steel material to be joined and the conditions of linear friction welding, and there are cases where it is lower than that of the base material portion 8 and cases where it is higher than that of the base material portion 8, but the hardness of the heat affected zone 6 is Lower than the material portion 8 .
• the decrease in the hardness of the heat affected zone 6 becomes significant when the hardness of the steel material is high (when the strength is high).
• the A1 point temperature of the preferred steel material, the additive element that exhibits secondary hardening, the hardness distribution of the linear friction welded joint 10, etc. are the same as in the case of friction stir welding, but in linear friction welding, the welding temperature (max temperature of the bonding interface 12) can be accurately controlled. That is, it is possible to control the maximum softening region in the heat affected zone 6 (the region where the highest temperature reached during welding is the A1 point temperature of steel) by the welding pressure. Further, by setting the highest temperature reached at the joint interface 12 to be equal to or higher than the A1 point temperature of the steel material, a region is formed in which the highest reached temperature of the heat affected zone 6 is the A1 point temperature of the steel material.
• the bonding temperature can be controlled by setting the bonding pressure during linear friction welding to a value equal to or higher than the yield stress of the material to be welded at the desired welding temperature and to the tensile strength or lower.
• the bonding pressure is equal to or higher than the yield stress of the material to be bonded, burrs start to be discharged from the interface to be bonded, and when the bonding pressure is increased until the tensile strength is reached, the discharge of burrs is accelerated.
• the tensile strength at a specific temperature is also substantially constant depending on the materials to be joined, so a joining temperature corresponding to the set joining pressure can be achieved. From the viewpoint of suppressing an increase in bonding temperature, it is preferable to set the bonding pressure to be equal to or lower than the tensile strength.
• the macrostructure of the cross section of the joint (cross section perpendicular to the joint line) obtained when the maximum temperature reached at the joint interface 12 during welding at the joint interface 12 is the A1 point temperature of the steel material due to the welding pressure during linear friction welding.
• FIG. 3 Schematically shown in FIG.
• the lower portion of FIG. 3 also schematically shows the hardness distribution corresponding to the cross-sectional macrostructure.
• the hardness distribution is the hardness distribution along the dashed-dotted line of the cross section. If the highest temperature reached during welding at the joint interface 12 is assumed to be the A1 point temperature of the steel material, the joint interface 12 becomes the most softened region.
• Solid Phase Welded Joint Embodiments of the solid phase welded joint of the present invention will be described in detail, taking solid phase welded joints obtained by using friction stir welding and linear friction welding as solid phase welding methods as representatives.
• Figs. 4 and 5 show schematic diagrams of a solid phase welded joint obtained by friction stir welding and a solid phase welded joint obtained by linear friction welding, respectively.
• a friction stir welded joint 2 is formed with a friction stir portion 4 , a heat affected zone 6 exists on the outer edge of the friction stir welded portion 4 , and a base material portion 8 is formed on the outer side of the heat affected zone 6 .
• a joint interface 12 is formed in the linear friction-joint joint 10 , a heat-affected zone 6 exists on the outer edge of the joint interface 12 , and a base material portion 8 is formed outside the heat-affected zone 6 .
• At least one of the materials to be joined is a steel material
• the steel material has an additive element that develops secondary hardening
• the A1 point temperature of the steel material is 400 to 650 ° C.
• the heat The Vickers hardness difference between the most softened region in the affected portion 6 and the base material portion 8 is 100 HV or less.
• the Vickers hardness difference between the most softened region and the base material portion 8 is more preferably 75 HV or less, most preferably 50 HV or less.
• the Vickers hardness of the most softened region is 450 HV or more.
• a Vickers hardness of 450 HV or more in the most softened region a solid-phase welded joint that fully utilizes the mechanical properties of the material to be welded even when ultra-high-strength steel is used as the material to be welded.
• the Vickers hardness of the most softened region is more preferably 500 HV or higher, most preferably 550 HV or higher.
• the steel material that has been solid-phase-bonded contains additional elements that cause secondary hardening, and the softening of the most softened region is suppressed by the secondary hardening.
• the additive element is not particularly limited as long as it does not impair the effects of the present invention, and various conventionally known additive elements for secondary hardening of steel can be used, but V, W and Mo are preferably used. Since the steel containing these elements exhibits significant secondary hardening due to fine precipitates, softening in the heat affected zone 6 can be effectively suppressed. A more preferable additive element is V.
• a steel plate (comparative steel plate 1) of 3 mm was subjected to friction stir welding.
• the hot-rolled steel material was air-cooled, subjected to solution treatment at 1000° C. for 10 minutes, and then water-cooled to obtain a steel sheet.
• a cemented carbide tool was used for the friction stir welding, and the welding conditions were a rotation speed of 400 rpm, a welding speed of 150 mm/min, and a welding load of 2.5 tons.
• the tool used has a shoulder diameter of 15 mm, a probe diameter of 6 mm and a probe length of 2.9 mm.
• FIG. 6 shows the hardness distribution of the cross section orthogonal to the joint portion of the obtained joint.
• the hardness of the most softened region in the heat affected zone is 340 HV, indicating significant softening.
• the highest temperature reached was 658° C., which is the A1 point temperature of the steel material.
• Fig. 7 shows the hardness distribution of the cross section perpendicular to the joint of the obtained joint.
• the Vickers hardness (about 500 HV) of the base metal is equivalent to that of Comparative Steel Plate 1, but the hardness of the most softened region in the heat affected zone is 435 HV, indicating that softening is suppressed.
• the result of the comparative steel plate 1 is also shown for comparison in FIG.
• Fig. 8 shows the hardness distribution of the cross section perpendicular to the joint part of the obtained joint.
• the hardness of the most softened region in the heat-affected zone was 420 HV, which was almost the same as that of comparative steel plate 2, and no improvement in the softening suppressing effect due to an increase in the amount of V added was observed.
• FIG. 8 also shows the results of comparative steel sheets 1 and 2 for comparison.
• the A1 point temperature of comparative steel plate 3 is 734°C, but the temperature at which secondary hardening by V remarkably occurs is said to be about 600°C (Masashi Maki, Structural Control of Steel, Uchida O. Jianpo (2015) 98-101). Therefore, by increasing the Mn amount of the comparative steel plate 3 to 4.0% by mass, C (0.2% by mass)-Si (2.0% by mass)-Mn (4.0% by mass)-V (1.0% by mass) 0% by mass)-Fe (Bal.)-Fe (Bal.) composition and having a thickness of 3 mm (implementation steel plate) was manufactured, and friction stir welding was performed on the steel plate under the same conditions as in the case of the comparative steel plate 1.
• the A1 point temperature of the working steel sheet decreased as the amount of Mn increased, reaching 572°C.
• the manufacturing conditions of the steel plate are the same as those of the comparative steel plate 3.
• Fig. 9 shows the hardness distribution of the cross section orthogonal to the joint part of the obtained joint.
• the hardness of the most softened region in the heat-affected zone is 465 HV, indicating that softening is remarkably suppressed.
• the results show that a joint efficiency of about 90% can be obtained for 1.5 GPa class high-strength steel sheets.
• the result of the comparative steel plate 3 is also shown for comparison in FIG.
• FIGS. 10 and 11 Scanning transmission electron microscope (STEM) observation images of the heat-affected zones of comparative steel sheets 1 and 2 are shown in FIGS. 10 and 11, respectively.
• STEM Scanning transmission electron microscope
• the maximum softening region in the solid phase joint of steel is the region where the maximum temperature reached during joining is the A1 point temperature of the steel, and an element that causes secondary hardening is added to the steel. , it became clear that the softening of the heat-affected zone is extremely effectively suppressed by joining so that secondary hardening occurs at the A1 point temperature.

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• 2023
  • 2023-01-16 JP JP2024502897A patent/JPWO2023162502A1/ja active Pending
  • 2023-01-16 WO PCT/JP2023/000938 patent/WO2023162502A1/ja not_active Ceased

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