WO2013137249A1 - 鉄鋼材の製造方法 - Google Patents

鉄鋼材の製造方法 Download PDF

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Publication number
WO2013137249A1
WO2013137249A1 PCT/JP2013/056800 JP2013056800W WO2013137249A1 WO 2013137249 A1 WO2013137249 A1 WO 2013137249A1 JP 2013056800 W JP2013056800 W JP 2013056800W WO 2013137249 A1 WO2013137249 A1 WO 2013137249A1
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WO
WIPO (PCT)
Prior art keywords
base material
steel material
cooling
austenite
strain
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Ceased
Application number
PCT/JP2013/056800
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English (en)
French (fr)
Japanese (ja)
Inventor
藤井　英俊
好昭 森貞
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The University of Osaka
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Osaka University NUC
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Filing date
Publication date
Application filed by Osaka University NUC filed Critical Osaka University NUC
Priority to CN201380014331.4A priority Critical patent/CN104204233B/zh
Priority to US14/384,876 priority patent/US9617613B2/en
Priority to KR1020147027871A priority patent/KR102095607B1/ko
Priority to IN1789MUN2014 priority patent/IN2014MN01789A/en
Publication of WO2013137249A1 publication Critical patent/WO2013137249A1/ja
Anticipated expiration legal-status Critical
Ceased legal-status Critical Current

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    • 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
    • C21D8/00—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • 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
    • B23K20/122—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 using a non-consumable tool, e.g. friction stir 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
    • C21D9/50—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for welded joints
    • 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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/001—Austenite
    • 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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/008—Martensite
    • 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
    • C21D7/00—Modifying the physical properties of iron or steel by deformation
    • C21D7/02—Modifying the physical properties of iron or steel by deformation by cold working
    • C21D7/04—Modifying the physical properties of iron or steel by deformation by cold working of the surface
    • 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

Definitions

  • An embodiment of the present invention relates to a method for manufacturing a steel material, and relates to a method for manufacturing a steel material that manufactures a steel material having increased strength and ductility by processing a base material of the steel material.
  • Friction Stir Welding has various excellent properties including joint properties, and has been applied to aluminum alloys in various industrial fields soon after being developed.
  • FSW Friction Stir Welding
  • One embodiment of the present invention has been made in view of the above problems, and an object thereof is to provide a method for producing a steel material capable of producing a steel material having high ductility while having high strength. To do.
  • a heating step of heating A above point C1 is the temperature at which the base material of the steel material austenite appears
  • the M f point is the temperature at which the tissue entirely is the martensite matrix steel
  • the amount of strain estimated to drop below the temperature at which the material is used and in the region where martensite is generated in the base material on the continuous cooling transformation diagram (CCT diagram)
  • a method of manufacturing a steel material including a cooling step of cooling a base material subjected to a heating step and a strain introduction step to a temperature higher than the Mf point at a cooling rate estimated to intersect lines extrapolating a cooling curve. is there.
  • the steel base material is heated to the AC1 point or higher, which is the temperature at which austenite appears. Thereby, austenite can appear in the base material.
  • strain introduction step the distortion amount of M f point organization entire preform is at a temperature of the martensite is estimated that falls below the temperature at which the steel material is used to introduce the base material. For this reason, it is possible to prevent the entire structure of the steel material from becoming martensite when the steel material is cooled to a temperature at which the steel material is used, such as room temperature.
  • the region where ferrite or pearlite is generated also expands.
  • a continuous cooling transformation diagram showing the phase transformation when the steel base material is continuously cooled on the coordinate plane of time and temperature is shown.
  • it further includes an inspection process for inspecting the structure of the base material that has been subjected to the cooling process, and it is found that no austenite remains in the base material structure and martensite is generated in the inspection process.
  • an inspection process for inspecting the structure of the base material that has been subjected to the cooling process, and it is found that no austenite remains in the base material structure and martensite is generated in the inspection process.
  • the inspection process which inspects the structure
  • the M f point is not sufficiently lowered with respect to the temperature at which the steel material is used. Is estimated. Therefore, when manufacturing the steel material next time, an increase in the amount of strain to be introduced into the base material in the strain introduction process, and the addition amount of austenite stabilizing elements such as C, Mn, Ni, Cr and Mo to the base material At least one of the increases is performed. Thereby, the Mf point can be sufficiently lowered with respect to the temperature at which the steel material is used, and austenite can remain.
  • the base material is heated and the strain is introduced into the base material by rotating the rotary tool while bringing the tip of the rod-shaped rotary tool into contact with the base material, and the cooling step. Then, at least one of moving the tip of the rotary tool while rotating the rotary tool while the tip of the rotary tool is in contact with the base material and separating the tip of the rotary tool from the base material.
  • the base material can be cooled.
  • the base material is heated and the strain is introduced into the base material by rotating the rotary tool while bringing the tip of the rod-shaped rotary tool into contact with the base material.
  • the tip of the rotating tool is moved while the rotating tool is rotated while the tip of the rotating tool is in contact with the base material, and the tip of the rotating tool is separated from the base material.
  • the base material is cooled by at least one of them.
  • FIG. 1 is a state diagram of a steel material 1. It is a CCT figure of steel material 2. It is a figure which shows the effect
  • FIG. 3 is a table showing the chemical composition of steel material 1 in Experimental Example 1.
  • (A)-(d) shows the phase map of the stirring part of the steel material 1 in Experimental Example 1, and shows the phase map of the stirring part at the rotation speeds of 100 rpm, 200 rpm, 300 rpm, and 400 rpm, respectively.
  • FIG. 6 is a diagram showing an EBSD phase distribution image of a stirring portion at a rotational speed of 400 rpm and a joining speed of 100 mm / min of the steel material 2 in Experimental Example 2.
  • FIG. 7 is a diagram showing an EBSD phase distribution image of a stirring portion at a rotation speed of 400 rpm and a joining speed of 400 mm / min of the steel material 2 in Experimental Example 2. It is a graph which shows the base material of the steel material 2 in Experimental example 2, and the nominal stress-nominal strain curve at a rotational speed of 400 rpm and a joining speed of 400 mm / min. It is a figure which shows the fcc orientation map of the base material of the steel material 3 in Experimental example 2.
  • FIG. 10 is a diagram showing an fcc orientation map of a base material at a rotational speed of 200 rpm and a joining speed of 400 mm / min of the steel material 3 in Experimental Example 2.
  • FIG. 10 is a diagram showing an fcc orientation map of a base material at a rotational speed of 300 rpm and a joining speed of 400 mm / min of the steel material 3 in Experimental Example 2.
  • FIG. 10 is a diagram showing an fcc orientation map of a base material at a rotational speed of 400 rpm and a joining speed of 400 mm / min of the steel material 3 in Experimental Example 2. It is a table
  • FIG. It is a graph which shows the XRD pattern of the stirring part in the different rotational speed in Experimental example 3.
  • the base materials 1a and 1b for example, ferritic steel, Cr—Mo steel and high carbon steel can be used.
  • the additive 10 can be filled on the stirring portion 20 of the base materials 1a and 1b depending on the situation.
  • powdery or granular C, Mn, Ni, Cr, Mo, W, V, Ta, or the like can be used.
  • C, Mn, Ni, Cr, Mo, W, V, Ta, etc. in the form of a plate or a thin sheet are formed on the base materials 1 a and 1 b other than the stirrer 20 or the stirrer 20. It may be arranged on the surface.
  • the additive 10 is not restricted to the stirring part 20, You may be added to the whole composition of the base materials 1a and 1b.
  • the stirring unit 20 is forcibly cooled from the outside by circulating a cooled refrigerant on the upper surface or the lower surface of the stirring unit 20.
  • Cooling means may be arranged.
  • a cooling means in this case, for example, liquid CO 2 , liquid nitrogen, water, and the like can be supplied to the stirring unit 20.
  • a rotating tool 100 as shown in FIG. 2 is prepared.
  • the rotary tool 100 has a substantially cylindrical shape, and includes a substantially cylindrical probe 102 having a smaller diameter than the shoulder 101 at the tip.
  • the material of the rotary tool 100 is made of, for example, tool steel such as SKD61 steel compliant with Japanese Industrial Standards, cemented carbide containing tungsten carbide (WC) as a main component, or ceramic such as Si 3 N 4. Can be.
  • C1-point A of each composition of the steel material can be obtained by the following equation (1).
  • the amount of heat input Q to the stirring unit 20 during the friction stirring process can be obtained by the following equation (2).
  • the amount of M f point that is a temperature at which the entire structure of the base materials 1a and 1b becomes martensite is estimated to be lower than the temperature at which the steel material is used.
  • austenite remains in the structure of the stirring unit 20 of the base materials 1a and 1b (S102).
  • FIG. 6 when strain is introduced into the stirring portions 20 of the base materials 1a and 1b, the M s point, which is the temperature at which martensite appears, decreases.
  • the M f point (not shown), which is a temperature lower than the M s point and at which the entire structure of the base materials 1a and 1b becomes martensite, also decreases.
  • both the M f point and the M s point are lowered to a temperature lower than room temperature (20 ° C.).
  • room temperature 20 ° C.
  • it is possible to leave austenite at the temperature at which the steel material is used by lowering the Mf point below the temperature at which the steel material is used.
  • the M s point can be lowered below the temperature at which the steel material is used.
  • the strain is introduced into the stirring unit 20 of the base materials 1a and 1b by rotating the probe 102 at the tip of the rotary tool 100 while contacting the stirring unit 20 of the base materials 1a and 1b. It can be performed in one process simultaneously with heating to the AC 1 point or higher.
  • the amount of strain introduced using the friction stir welding technique can be obtained by the following equation (4).
  • ⁇ is a strain (in the following equation, strain rate, which is the amount of strain introduced per unit time obtained by differentiating ⁇ with respect to time), and R m is 1 / of the rotational speed of the rotary tool 100.
  • r e is the effective (average) radius of the stirring unit 20
  • L e is the effective (average) depth of the stirring unit 20.
  • the stirring unit 20 of the base materials 1a and 1b is cooled to a temperature at which the steel material is used (S103).
  • S103 a temperature at which the steel material is used
  • the stirrer 20 of the base materials 1a and 1b is completed within the region where pearlite is generated in the stirrer 20 of the base materials 1a and 1b on the CCT diagram as shown in FIG. 6, the stirrer of the base materials 1a and 1b is completed.
  • the structure of the part 20 becomes pearlite and no austenite remains.
  • the cooling curves of the stirring parts 20 of the base materials 1 a and 1 b are shown in the region where the martensite of the stirring parts 20 of the base materials 1 a and 1 b is generated on the CCT diagram. Due to the cooling rate estimated that the extrapolated lines intersect, the stirring portions 20 of the base materials 1a and 1b are cooled to a temperature that is at least higher than the Mf point, for example, higher than the Ms point (S103). Thereby, austenite remains in the stirring part 20 of the base materials 1a and 1b after cooling.
  • the cooling of the stirrer 20 of the base materials 1a and 1b is performed in a state where the probe 102 at the tip of the rotary tool 100 is in contact with the stirrer 20 of the base materials 1a and 1b and rotated.
  • the cooling speed can be increased by increasing the rotational speed or moving speed (joining speed) of the rotating tool 100, and the cooling speed can be decreased by decreasing the rotating speed or moving speed (joining speed) of the rotating tool 100.
  • a sample of the stirring unit 20 of the base materials 1a and 1b is collected, and the sample structure is inspected (S104).
  • the specimen can be inspected by, for example, EBSD (Electron Back-Scatter Diffraction) or XRD (X-ray Diffraction).
  • EBSD Electro Back-Scatter Diffraction
  • XRD X-ray Diffraction
  • austenite remains in the structure of the examined specimen (S105)
  • the rotational tool 100 which is the condition of the strain amount introduced in S102 and the cooling rate in S103 is used.
  • the diameter of the shoulder 101, the diameter of the probe 102, the length of the probe 102, the rotational speed and the moving speed are maintained (S106).
  • the amount of strain can be increased by increasing the number of rotations of the rotary tool 100, increasing the diameter of the shoulder 101, and increasing the diameter of the probe 102.
  • the amount of strain can also be increased by lowering the temperature of the stirring unit 20 in the friction stirring process.
  • the M s point decreases as the amount of C added increases, and therefore the M s point can be further decreased by increasing the amount of C in the additive 10. It becomes possible.
  • the effect of lowering the M s point and the M f point has the greatest influence on the amount of addition of C. Therefore, by controlling the amount of C in the additive 10, the reduction of the M s point and the M f point can be reduced. The degree can be controlled.
  • Mn in additive 10 Ni by increasing either the amount of Cr and Mo, it is possible to increase the degree of reduction of the M s point and M f point.
  • the increase in the cooling rate is realized by increasing the rotational speed or moving speed (joining speed) of the rotary tool 100. Or it implement
  • the region where pearlite or ferrite is generated is an element having an atomic radius larger than that of Fe such as Mo, W, V, and Ta in the additive 10 to the base materials 1a and 1b. It decreases as the amount of elements that inhibit diffusion transformation increases.
  • FIG. 6 when strain is introduced into the stirring unit 20, a region where pearlite or ferrite is generated is increased accordingly, but larger than Fe such as Mo, W, V, and Ta. When atoms are added, it is considered that the diffusion transformation is inhibited and the action of increasing the region where pearlite or ferrite is generated is suppressed.
  • ferrite or pearlite is generated even at the same cooling rate by increasing the amount of an element having a larger atomic radius than Fe that inhibits the diffusion transformation such as Mo, W, V, and Ta in the additive 10.
  • the cooling can be terminated not in the region where the austenite is left but in the region where the austenite remains.
  • the following steel material is manufactured under the conditions controlled as described above (S109). Even if austenite remains in S105, the process of S107 is performed when martensite is generated, and the process of S108 is performed when ferrite or pearlite is generated. Thus, in the production of the next steel material, a steel material in which more austenite remains can be produced.
  • the base materials 1a and 1b of the steel material are heated to the AC1 point or higher, which is the temperature at which austenite appears (S101). Thereby, austenite can appear in the base materials 1a and 1b.
  • An amount of strain estimated to decrease the Mf point, which is the temperature at which the entire structure of the base materials 1a and 1b becomes martensite, falls below room temperature is introduced into the base material (S102). For this reason, it is possible to prevent the entire structure of the steel material from becoming martensite when the steel material is cooled to room temperature.
  • CCT diagram Continuous Cooling Transformation diagram
  • the strained austenite transforms into hard martensite, and the strength of the strained portion is improved. As a result, deformation of this portion is suppressed, and a TRIP effect is generated in which the transformation propagates to the untransformed austenite portion having a relatively low strength. For this reason, the steel material which has high ductility while having high intensity
  • the steel material is subjected to a treatment globally or locally to increase the strength. It is possible to make a steel material having strength and high ductility. For example, in a specific part of a structural member of an automobile, it is necessary to protect the occupant by absorbing the impact with high ductility while maintaining the shape of the vehicle body with high strength against the impact at the time of collision. However, according to the present embodiment, it is possible to add a local treatment to a specific part of the base material of the steel material so that only the specific part has high strength and high ductility.
  • tissue of the base materials 1a and 1b is further included (S104).
  • S105 When it is found that no austenite remains in the structure of the base material and martensite is generated (S105), it is estimated that the Mf point is not sufficiently lowered with respect to room temperature. Therefore, when the steel material is manufactured next time, the amount of strain introduced into the base materials 1a and 1b in S102 and austenite stabilization such as C, Mn, Ni, Cr and Mo to the base materials 1a and 1b are increased. At least one of the addition amounts of the elements is increased (S107). Thereby, the Mf point can be sufficiently lowered with respect to room temperature, and austenite can be left.
  • the base materials 1a and 1b are heated and applied to the base materials 1a and 1b.
  • the base material 100 is cooled by introducing strain and moving the tip of the rotary tool 100 while rotating the rotary tool 100 while the tips of the rotary tool 100 are in contact with the base materials 1a and 1b.
  • heating, strain introduction, and cooling can be performed in one process.
  • the friction stir welding technique it becomes easy to locally heat the base materials 1a and 1b and to locally introduce strain into the base materials 1a and 1b.
  • the cooling rate can be easily controlled by adjusting the moving speed of the tip of the rotary tool 100 and the rotational speed of the rotary tool 100.
  • this invention is not limited to the said embodiment, A various deformation
  • the base materials 1a and 1b are moved by moving the tip of the rotary tool 100 while the rotary tool 100 is rotated while the tip of the rotary tool 100 is in contact with the base materials 1a and 1b.
  • the aspect which joined steel and produces steel materials in the stirring part 20 by joining was mainly demonstrated.
  • the distal end portion of the rotary tool 100 is rotated at one or more sites in a state where the rotary tool 100 is rotated while the distal end portion of the rotary tool 100 is in contact with the base materials 1a and 1b.
  • a steel material may be generated in the stirring unit 20 by a spot-type friction stir welding technique to be stopped.
  • the base materials 1a and 1b can be cooled by separating the tip of the rotary tool 100 from the base materials 1a and 1b.
  • the cooling rate can be controlled by adjusting the pulling speed, rotating speed, and the like of the rotary tool 100.
  • the plate-like base materials 1a and 1b are overlapped, and the powdery or granular additive 10 is filled between them, or the plate-like or sheet-like additive 10 is placed and stirred. Even if the friction stir processing is performed in a manner similar to the superposition joining in which the stirring unit 20 is stirred by rotating the rotating tool 100 in contact with the base material 1a and moving it on the base material 1a. good. Also in this case, a spot-type friction stirring process without the movement of the rotary tool 100 can be performed.
  • the rotary tool 100 is brought into contact with the base 1a.
  • the structure of the stirring unit 20 may be modified by causing the stirring unit 20 to generate a steel material by stirring the stirring unit 20 by rotating and rotating the base material 1a. Also in this case, a spot-type friction stirring process without the movement of the rotary tool 100 can be performed. In the above-described various friction stir welding and friction stir processing, the arrangement of the additive 10 can be omitted if unnecessary.
  • the embodiment of the present invention is not limited to this, and the friction stir processing is performed by performing heating, introduction of strain and cooling to the base material of the steel material so as to meet the conditions specified in the embodiment of the present invention. It is possible to manufacture a steel material having high strength and high ductility.
  • the heating of the base material of the steel material can also be performed by a predetermined heat source or the like.
  • the introduction of strain into the base material of the steel material can also be performed by processes such as rolling and forging.
  • the base material of the steel material can be cooled by a predetermined cooling means.
  • the rotational speed was 100 to 400 rpm, and the joining speed was constant at 100 mm / min.
  • the steel material 1 is at 750 ° C. or higher, the steel material 1 is easily softened rapidly, so that the load was reduced as much as possible.
  • argon gas was used as a shielding gas at a flow rate of 30 l / min to prevent oxidation of the rotating tool and the stirring unit.
  • a water-cooled cooling holder was installed to cool the rotating tool and the joining device.
  • the stirring unit was inspected. As shown in the phase maps of FIGS. 11 (a) to 11 (d), the structure of the base material of the steel material 1 is ferrite and tempered martensite. It can be confirmed that the amount of retained austenite shown in gray in the three colors of white increases.
  • the joint was inspected by EBSD.
  • the base material of the steel material 2 shown in FIG. 16 and the joint portion of the steel material 2 shown in FIG. 17 under the condition of rotational speed 400 rpm ⁇ joining speed 100 mm / min there is little residual austenite shown in gray in the figure. I understand.
  • Tensile tests were performed on the joints obtained from the base metal and each joining speed. As shown in FIG. 19, it can be seen that the joint having a large amount of retained austenite and a joining speed of 400 mm / min is improved in both strength and ductility as compared with the base material.

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PCT/JP2013/056800 2012-03-14 2013-03-12 鉄鋼材の製造方法 Ceased WO2013137249A1 (ja)

Priority Applications (4)

Application Number Priority Date Filing Date Title
CN201380014331.4A CN104204233B (zh) 2012-03-14 2013-03-12 钢铁材料的制造方法
US14/384,876 US9617613B2 (en) 2012-03-14 2013-03-12 Method for manufacturing ferrous material
KR1020147027871A KR102095607B1 (ko) 2012-03-14 2013-03-12 철강재의 제조 방법
IN1789MUN2014 IN2014MN01789A (cg-RX-API-DMAC10.html) 2012-03-14 2013-03-12

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JP2012057986A JP5900922B2 (ja) 2012-03-14 2012-03-14 鉄鋼材の製造方法
JP2012-057986 2012-03-14

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JP2018016866A (ja) * 2016-07-29 2018-02-01 国立大学法人大阪大学 摩擦攪拌接合用鋼及び摩擦攪拌接合方法

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US11794271B2 (en) * 2018-07-19 2023-10-24 Nippon Light Metal Company, Ltd. Method for manufacturing liquid-cooled jacket
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KR102147609B1 (ko) 2019-12-12 2020-08-24 박성룡 프레스 금형용 철강 제조 공정을 위한 제어 방법 및 장치
JP7347234B2 (ja) * 2020-01-24 2023-09-20 日本軽金属株式会社 液冷ジャケットの製造方法及び摩擦攪拌接合方法
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