JP2014105379A - Ni-BASED ALLOY, FRICTION STIR WELDING TOOL USING THE SAME, AND METHOD FOR PRODUCING THE SAME - Google Patents

Abstract

PROBLEM TO BE SOLVED: To provide a Ni-based alloy, a friction stir welding tool using the same, and a method for producing the same, of which hardness can ensure Vickers hardness of about Hv600 (Rockwell hardness HRC55) at temperatures above 500°C and which easily enables the reproduction of only the tip part of a probe.SOLUTION: A Ni-based alloy consisting of Al in composition range of 2 wt.% or more and 4 wt.% or less, Ta in composition range of 14 wt.% or more and 16 wt.% or less, V in composition range of 10 wt.% or more and 12 wt.% or less, B in composition range of 0.003 wt.% or more and 0.01 wt.% or less, and Ni of balance, and exhibiting 2-overlapping-phase structure having a phase consisting of an intermetallic compound between Ni and Al and a phase consisting of an intermetallic compound between Ni and V, is used, in a friction stir welding tool 1.

Description

  The present invention relates to a Ni-based alloy, a friction stir welding tool using the same, and a method for manufacturing the same, and in particular, a Ni-based alloy having excellent wear resistance at high temperatures, a friction stir welding tool using the same, and the tool. It relates to a manufacturing method.

  In recent years, a friction stir welding apparatus has been proposed in which a predetermined joint portion in a workpiece to be processed consisting of a plurality of metal plates such as an iron plate and an Al plate is frictionally stirred with a probe that rotates at high speed, and the metal plates are joined together. In addition, a configuration having a joint portion joined by a friction stir welding apparatus has been realized even in a strength part of a moving body such as an automobile.

  In such a friction stir welding apparatus, the probe inserted into the processing target component is moved relative to the processing target component while rotating at high speed, and a predetermined part is bonded. It is important to be composed of high material.

  Under such circumstances, Patent Document 1 is not related to a friction stir welding apparatus, but when joining a steel material that is a dissimilar metal to a Ni-base superalloy by welding, a metal and a Ni-base supermetal are combined. Turbine impeller 4 which is a Ni-based superalloy for the purpose of providing a welding method of steel material to a Ni-based superalloy and a welded joint capable of obtaining a sound welded joint without cracks at the boundary with the alloy And the rotor shaft 2, which is a steel material, are joined to each other by welding at the respective boundary portions, the irradiation position of the electron beam EB is controlled, and the Ni-base superalloy of the turbine impeller 4 and the rotor shaft 2 are controlled. The structure which made the mixing ratio of the weld metal 6 melted together in the boundary part with this steel material 0.5-0.8 is disclosed.

  Patent Document 2 also does not relate to a friction stir welding apparatus, but when joining a steel material, which is a dissimilar metal, to a Ni-base superalloy by welding, For the purpose of providing a welding method of a steel material to a Ni-base superalloy capable of obtaining a sound welded joint having no crack at the boundary and a welded joint, a turbine impeller 4 that is a Ni-base superalloy, and steel When the rotor shaft 2 which is a material is melted and joined to each other by welding at each boundary portion, the weld metal 6 in which the Ni-base superalloy of the turbine wheel 4 and the steel material of the rotor shaft 2 are melted together, and the turbine blade The structure which irradiates the boundary part with the vehicle 4 while deflecting the electron beam EB periodically is disclosed.

JP 2012-61498 A JP 2012-61499 A

  Here, according to the inventor's study, when friction stir welding is performed between Al alloys, since the Al alloy has low deformation resistance, hot tool steel or the like is used for the friction stir welding tool. . However, from the viewpoint of diversification of vehicle body design in recent years, there is an increasing demand for joining different materials such as combining a high-strength steel plate with an Al alloy. When the friction stir welding tool probe is inserted into the Al alloy and the high-tensile steel plate and stirred while rotating at a high speed, the temperature of the stirring portion becomes 500 ° C. or higher. At such a temperature, the temperature exceeds the tempering temperature of the hot work tool steel, so that its hardness decreases rapidly and wear tends to increase.

  On the other hand, as disclosed in Patent Document 1 and Patent Document 2, it has been proposed to use a Ni-base superalloy in a turbine impeller such as a jet engine. As such a Ni-base superalloy, specifically, Discloses that Mar-M246, which is a Mar-M material, is used.

  The chemical components of Mar-M246 are 0.15 wt% C, 9 wt% Cr, 10 wt% Co, 2.5 wt% Mo, 10 wt% W, 1.5 wt% Ta, 1.5 wt% Ti. , Al is composed of 5.5 wt% and the balance Ni, and such Mar-M246 can be used for a turbine impeller, so it is surely excellent in heat resistance.

  However, since Mar-M246 has a low hardness of about Vickers hardness Hv400 (Rockwell hardness HRC41), Mar-M246 was used as a probe for friction stir welding with an Al alloy and a high-tensile steel plate. In some cases, the wear increases.

  In other words, at present, the Ni-base superalloy with the Ni-base superalloy having improved hardness while maintaining the heat resistance, specifically, the hardness is about Vickers hardness Hv600 (Rockwell hardness HRC55) at a temperature of 500 ° C. or higher. There is a demand for a Ni-based alloy having a new structure.

  In addition, the only part of the probe that wears during friction stir welding is the tip of the probe that is inserted into the member to be processed made of an Al alloy, a high-tensile steel plate, etc., so that only the tip of the worn probe can be reproduced. If it is possible simply, there is no need to reproduce the entire probe, and the cost of friction stir welding can be reduced by reducing the manufacturing cost.

  Therefore, at present, Ni has a novel structure that can secure a Vickers hardness of about Hv600 (Rockwell hardness HRC55) at a temperature of 500 ° C. or higher, and can easily reproduce only the tip of the probe. There is a desire for a base alloy.

  The present invention has been made through the above-described studies. The hardness of the present invention can be ensured to be approximately Vickers hardness Hv600 (Rockwell hardness HRC55) at a temperature of 500 ° C. or more, and it is easy to reproduce only the tip of the probe. It is an object of the present invention to provide a Ni-based alloy, a friction stir welding tool using the same, and a method for manufacturing the same.

  In order to achieve the above object, the Ni-based alloy according to the first aspect of the present invention includes Al in the component range of 2 wt% to 4 wt%, Ta in the component range of 14 wt% to 16 wt%, 10 wt% to 12 wt%. V of the following component range, B of the component range of 0.003 wt% or more and 0.01 wt% or less, and the balance Ni, the phase composed of the intermetallic compound of Ni and Al and the Ni and V And exhibiting a double-phase structure having a phase composed of an intermetallic compound.

  The friction stir welding tool according to the second aspect of the present invention includes a probe that can enter the workpiece to be processed during friction stir welding, and the probe includes the Ni-based alloy according to the first aspect.

  In addition to the second aspect, the present invention includes a probe main body and a tip layer laminated on the probe main body, and the tip layer is made of the Ni-based alloy. This is the third aspect.

Moreover, in addition to this 2nd or 3rd aspect, this invention makes it the 4th aspect that the said front end layer is a part which penetrate | invades with respect to the said process target component at the time of the said friction stir welding.

  In addition, the manufacturing method of the friction stir welding tool in the fifth aspect of the present invention includes Al in the component range of 2 wt% to 4 wt%, Ta in the component range of 14 wt% to 16 wt%, 10 wt% to 12 wt%. A raw material metal powder comprising V in the component range of B, B in the component range of 0.003 wt% or more and 0.01 wt% or less, and the balance Ni, and the main body member by mixing the raw metal powder into the carrier gas A step of disposing a nozzle member of a laser deposition device that can be ejected to an end of the main body member and capable of irradiating a laser beam to the end of the main body member so as to face the end of the main body member; A step of moving the nozzle member along the end of the main body member while ejecting the raw metal powder from the nozzle member and irradiating the laser beam; and And after the step of moving along the end of the main body member is completed, a solution treatment is performed on the built-up layer of the main body member, and the second to fourth steps are provided. A friction stir welding tool according to any aspect is manufactured.

  According to the configuration of the first aspect of the present invention, Al in the component range of 2 wt% to 4 wt%, Ta in the component range of 14 wt% to 16 wt%, V in the component range of 10 wt% to 12 wt%, 0 2 overlaps comprising B in the component range of 0.003 wt% or more and 0.01 wt% or less, and the balance Ni, a phase composed of an intermetallic compound of Ni and Al and a phase composed of an intermetallic compound of Ni and V By presenting a phase structure, it is possible to secure a hardness of about Vickers hardness Hv600 (Rockwell hardness HRC55) at a temperature of 500 ° C. or higher and easily reproduce only the tip of the probe of the friction stir welding tool. A Ni-based alloy can be realized.

  Further, according to the configuration in the second aspect of the present invention, the probe that can freely enter the workpiece to be processed at the time of friction stir welding includes the Ni-based alloy in the first aspect, so that the temperature is 500 ° C. or more. A friction stir welding tool having a probe that can secure a Vickers hardness of about Hv600 (Rockwell hardness HRC55) can be realized.

  According to the configuration of the third aspect of the present invention, the probe has a probe main body and a tip layer laminated on the probe main body, and the tip layer is made of such a Ni-based alloy. Only the tip of the probe can be easily reproduced.

  Further, according to the configuration of the fourth aspect of the present invention, since the tip layer is a part that enters the part to be processed at the time of friction stir welding, only the part that is consumed at the time of friction stir welding can be easily re-applied. Can be produced.

  Further, according to the configuration of the fifth aspect of the present invention, it is possible to reliably manufacture a friction stir welding tool having a probe that can secure a Vickers hardness Hv600 (Rockwell hardness HRC55) at a temperature of 500 ° C. or higher. it can.

It is a partial side view of the tool for friction stir welding in the embodiment of the present invention. It is an optical micrograph which shows the alloy structure of the state in which the tip layer of the probe of the friction stir welding tool of this embodiment was formed by laser deposition. It is an optical microscope photograph which shows the alloy structure of the state which carried out the solution treatment after the front-end | tip layer of the probe of the tool for friction stir welding in this embodiment was formed by laser deposition. It is a graph which shows the Vickers hardness of the probe of the tool for friction stir welding in this embodiment compared with the thing in a comparative example, a horizontal axis is temperature and a vertical axis | shaft is Vickers hardness. It is a graph which shows the creep tolerance temperature of the probe of the tool for friction stir welding in this embodiment compared with the thing in a comparative example. It is a schematic diagram which shows the process of forming a front-end | tip layer by the laser deposition method in the probe of the tool for friction stir welding in this embodiment. It is a side view which shows the state by which the front end layer was formed in the probe of the tool for friction stir welding in this embodiment.

  Hereinafter, a Ni-based alloy, a friction stir welding tool using the Ni-based alloy, and a manufacturing method thereof according to embodiments of the present invention will be described in detail with reference to the drawings as appropriate.

  First, the configuration of the Ni-based alloy and the friction stir welding tool using the same according to the present embodiment will be described in detail with reference to FIGS. 1 to 5.

  FIG. 1 is a partial side view of the friction stir welding tool in the present embodiment. FIG. 2 is an optical micrograph showing an alloy structure in a state where the tip layer of the probe of the friction stir welding tool of the present embodiment is formed by laser deposition. FIG. 3 is an optical micrograph showing the alloy structure in a state in which the tip layer of the probe of the friction stir welding tool in the present embodiment is formed by laser deposition and then subjected to a solution treatment. FIG. 4 is a graph showing the Vickers hardness of the probe of the friction stir welding tool in this embodiment in comparison with that in the comparative example, where the horizontal axis represents temperature and the vertical axis represents Vickers hardness. FIG. 5 is a graph showing the creep endurance temperature of the probe of the friction stir welding tool in this embodiment in comparison with that in the comparative example.

  As shown in FIG. 1, the friction stir welding tool 1 in this embodiment is typically made of an Al alloy and a high-tensile steel plate or the like during friction stir welding, and is inserted into a workpiece to be omitted (not shown) and rotated at high speed. The probe 10 is provided.

  The probe 10 typically includes a probe main body 12 made of hot tool steel and a tip layer 14 made of a Ni-based alloy and formed on the probe main body 12. If the reproduction of the probe 10 is not considered, the tip layer 14 may be omitted and the probe body 12 itself may be made of a Ni-based alloy. In such a case, the probe 10 is manufactured using a precision casting method. Can be done.

  The probe main body 12 is detachably and rotatably held by a holder 18 that is fixed to the friction stir welding apparatus (not shown), and is connected to a drive unit of the friction stir welding apparatus to be attached to a workpiece. It can move forward and backward and rotate freely.

  The tip layer 14 is integrally formed with the probe body 12 and is typically a layer formed by solution treatment of the laser deposition layer, and is a portion that is inserted into the workpiece to be processed during friction stir welding. It is. When viewed microscopically, the dilution layer 16 exists between the probe body 12 and the tip layer 14, but the thickness thereof is very small and does not affect various characteristics of the probe 10.

  Specifically, the chemical components of the Ni-based alloy constituting the tip layer 14 are Al in a component range of 2 wt% to 4 wt%, Ta in a component range of 14 wt% to 16 wt%, and 10 wt% to 12 wt%. It consists of V in the component range, B in the component range of 0.003 wt% or more and 0.01 wt% or less, and the balance Ni adjusted to be 100 wt% in combination with these chemical components. Of course, such chemical components are allowed to contain inevitable mixtures.

Here, the Al component range is defined as 2 wt% or more and 4 wt% or less, the Ta component range is defined as 14 wt% or more and 16 wt% or less, and the V component range is defined as 10 wt% or more and 12 wt% or less. This is because it is a component range for forming a double-phase structure composed of a Ni ₃ Al phase and a Ni ₃ V phase, and if such a condition is not satisfied, such a double-phase structure is not substantially generated. . The reason why the B component range is defined as 0.003 wt% or more and 0.01 wt% or less is that if the content is less than 0.003 wt%, the so-called grain boundary strengthening effect cannot be obtained. On the contrary, it is because an unnecessary boride is formed.

Further, in the Ni-based alloy of the tip layer 14, in addition to the γ ′ phase that is a precipitated phase made of Ni ₃ Al, a γ ″ phase that is a precipitated phase made of Ni ₃ V exists (hereinafter, such Ni-based alloy). The tip layer 14 has a double-layer structure in which these two eutectoid phases function as a strengthening phase. These γ ′ and γ ″ phases are typically laser deposition layers. Obtained by solution treatment. Specifically, a mere laser deposition layer only exhibits a single phase that is an equiaxed grain structure of a solid solution as shown in FIG. 2, but the melting temperature of the laser deposition layer is further reduced slightly. When solution treatment is performed at a temperature lower than that, a double-phase structure in which a γ ′ phase and a γ ″ phase are formed as precipitated phases as shown in FIG. 3 can be exhibited. If not, the tip layer 14 may be omitted and the probe main body 12 itself may be made of a Ni-based alloy. In such a case, the probe 10 is manufactured by a precision casting method, but only two precision casting methods are used. Depending on the situation where the phase structure is not sufficiently obtained, a similar solution treatment may be performed to obtain a double-phase structure.

That is, a general Ni-base superalloy such as Mar-M246 is a single-phase structure strengthened alloy made of Ni ₃ Al and having a γ ′ phase. In order to increase the hardness of the alloy of the tip layer 14, From the viewpoint that it is necessary to consider two-phase precipitates, V is added in a component range of 10 wt% or more and 12 wt% or less as a chemical component of the alloy. By the addition of V, a γ ″ phase composed of Ni ₃ V is precipitated, and a Ni-based super superalloy having a dual-phase structure that exhibits a γ ″ phase in addition to a γ ′ phase is realized.

  Specifically, as shown in FIG. 4, at room temperature RT, compared to Mar-M246, which is a general Ni-base superalloy (plotted by x in the figure), the Ni-base super The alloy (plotted with black circles in the figure) has a hardness of about 1.5 times. Even at a high temperature of 500 ° C. or higher when the workpieces made of Al alloy and high-tensile steel plate are friction stir welded, the decrease in the hardness of the Ni-based super-superalloy of this embodiment shows a gradual trend, compared with Mar-M246. And the Ni base super super alloy of this embodiment is maintaining the hardness of about 1.5 times or more (Vickers hardness Hv200 or more). Further, as shown in FIG. 5, the creep endurance temperature of the Ni-base superalloy of this embodiment is also improved by about 70 ° C. compared to Mar-M246, which is a general Ni-base superalloy. As a result, the probe 10 to which the Ni-based super superalloy according to the present embodiment was applied was able to extend the junction length to about 7 times that of the probe to which Mar-M246 was applied.

  Hereinafter, the manufacturing method of the friction stir welding tool 1 in the present embodiment will be described in detail with reference to FIGS. 6 and 7. Here, since the life limit of the friction stir welding tool 1 is determined by the wear of the tip portion of the probe 10 inserted into the member to be processed, if only the tip portion of the probe 10 is reproduced, it can be used again. The following manufacturing method will be described with a configuration example for forming the tip layer 14 on the probe main body 12 by paying attention to the possibility.

FIG. 6 is a schematic diagram showing a step of forming a tip layer on the probe of the friction stir welding tool in this embodiment by a laser deposition method. FIG. 7 is a side view showing a state in which a tip layer is formed on the probe of the friction stir welding tool in the present embodiment.

  As shown in FIG. 6, first, the nozzle member 22 of the laser deposition apparatus 20 is disposed so as to face the upper surface of the main body member 112 made of hot tool steel. The nozzle member 22 has a central hole 24 that vertically penetrates the central portion thereof, and a peripheral hole 26 that surrounds the central hole 24 and penetrates the nozzle member 22 vertically.

  Next, the laser beam B is irradiated from the central hole 24 of the nozzle member 22 toward the upper surface of the main body member 112, and the laser beam B of the main body member 112 is irradiated from the peripheral hole 26 of the nozzle member 22. The nozzle member 22 is moved so that the entire upper surface of the main body member 112 is scanned while injecting the raw metal powder 28 mixed in an inert carrier gas such as Ar gas. At this time, a molten pool 113 in which the raw metal powder 28 is melted is formed on the upper surface of the main body member 112 to which the raw metal powder 28 is injected while being irradiated with the laser beam B. Along with this, the molten pool 113 is solidified and becomes a built-up layer 114 which is epitaxially grown on the upper surface of the main body member 112 and built up. A dilution layer 116 is formed below the build-up layer 114, but its thickness is very small.

  Here, the chemical components of the raw metal powder 28 are Al in a component range of 2 wt% or more and 4 wt% or less, Ta in a component range of 14 wt% or more and 16 wt% or less, and V in a component range of 10 wt% or more and 12 wt% or less. , B in the component range of 0.003 wt% or more and 0.01 wt% or less and the balance Ni adjusted to 100 wt% in combination with these chemical components, and the chemistry of the above-described Ni-based super-superalloy Same as ingredient.

  The scanning speed of the nozzle member 22 is preferably in the range of 300 mm / min to 800 mm / min. This is because if the scanning speed is less than 300 mm / min, the heat input to the upper surface of the main body member 112 is too large, and conversely if the scanning speed exceeds 800 mm / min, the heat input to the upper surface of the main body member 112 is too small. Therefore, such a range is preferable. The power of the laser beam B is preferably in the range of 300 W to 2000 W. This is because if the power of the laser beam B is less than 300 W, the upper surface of the main body member 112 cannot be sufficiently melted. Conversely, if the power of the laser beam B exceeds 2000 W, the upper surface of the main body member 112 becomes excessive. This is because such a range is preferable for melting. The spot diameter of the laser beam B is preferably in the range of 1 mm to 3 mm. This is because if the spot diameter of the laser beam B is less than 1 mm, the irradiation area on the upper surface of the main body member 112 is too small and the heat input becomes too large. Conversely, if the spot diameter of the laser beam B exceeds 3 mm, This is because such an area is preferable because the irradiation area with respect to the upper surface of the main body member 112 is too large and heat input is insufficient. The gas amount of the carrier inert gas is preferably in the range of 5 liters / minute to 25 liters / minute. The reason is that if the amount of gas is less than 5 liters / minute, the amount of the inert gas is too small and the upper surface of the main body member 112 is oxidized. This is because such a range is preferable.

  Next, when the nozzle member 22 finishes scanning the entire upper surface of the main body member 112 and the irradiation of the laser beam B and the injection of the raw metal powder 28 are stopped, a small thickness is formed on the main body member 112 as shown in FIG. The probe preliminary body 200 in which the build-up layer 114 is formed through the diluted layer 116 is obtained. The metal structure of the build-up layer 114 exhibited a single phase which is an equiaxed grain structure of a solid solution as shown in FIG.

Finally, a solution treatment for maintaining the probe preliminary body 200 at a temperature of 1280 ° C. for 3 hours is performed. The temperature of 1280 ° C. is set as a temperature immediately before the temperature at which the probe preliminary body 200 is melted when it is raised. As a result of the solution treatment, a probe 10 having a probe main body 12 corresponding to the main body member 112 and a tip layer 14 formed on the probe main body 12 and corresponding to the build-up layer 114 as shown in FIG. 1 is obtained. It is done. As shown in FIG. 3, the metal structure of the tip layer 14 is a double-phase structure in which a γ ′ phase that is a precipitated phase composed of Ni ₃ V is present in addition to a γ ′ phase that is a precipitated phase composed of Ni ₃ Al. It was made.

  According to the configuration of the present embodiment described above, Al in the component range of 2 wt% to 4 wt%, Ta in the component range of 14 wt% to 16 wt%, V in the component range of 10 wt% to 12 wt%, 0.003 wt % And 0.01 wt% or less of the component range B, and the balance Ni, the phase consisting of an intermetallic compound of Ni and Al and the phase consisting of an intermetallic compound of Ni and V , The hardness can be secured to a Vickers hardness Hv600 (Rockwell hardness HRC55) at a temperature of 500 ° C. or more, and only the tip 14 of the probe 10 of the friction stir welding tool 1 can be easily reproduced. A possible Ni-based super-superalloy can be realized.

  Further, according to the configuration of the present embodiment, the probe 10 that can penetrate into the workpiece to be processed at the time of friction stir welding includes such a Ni-based super-superalloy, so that the hardness is Vickers hardness Hv600 ( The friction stir welding tool 1 having the probe 10 that can secure about Rockwell hardness HRC55) can be realized.

  In addition, according to the configuration of the present embodiment, the probe 10 includes the probe main body 12 and the tip layer 14 laminated on the probe main body 12, and the tip layer 14 is made of such a Ni-based super super alloy. Thus, only the tip portion 14 of the probe 10 can be easily reproduced.

  In addition, according to the configuration of the present embodiment, the tip layer 14 is a part that intrudes into the workpiece to be processed at the time of friction stir welding, so that only the part that is consumed at the time of friction stir welding can be easily reproduced. Can do.

  The present invention is not limited to the above-described embodiments in terms of the shape, arrangement, number, etc. of the constituent elements, and departs from the gist of the invention, such as appropriately replacing the constituent elements with those having the same operational effects. Of course, it can be appropriately changed within the range not to be.

  As described above, in the present invention, at a temperature of 500 ° C. or higher, the hardness can be secured to about Vickers hardness Hv600 (Rockwell hardness HRC55), and it is possible to easily reproduce only the tip of the probe. Since it is possible to provide a base alloy, a tool for friction stir welding using the same, and a method for manufacturing the same, it is widely used for friction stir welding of strength parts of moving bodies such as automobiles from its general-purpose universal character. It is expected to be applicable to the field.

DESCRIPTION OF SYMBOLS 1 ... Tool for friction stir welding 10 ... Probe 12 ... Probe main body 14 ... Tip layer 16 ... Dilution layer 18 ... Holder 20 ... Laser deposition apparatus 22 ... Nozzle member 24 ... Central hole 26 ... Peripheral hole 28 ... Raw metal powder 112 ... Body member 113 ... Molten pool 114 ... Overlay layer 116 ... Dilution layer 200 ... Probe preliminary body B ... Laser beam

Claims (5)

  Al in a component range of 2 wt% to 4 wt%, Ta in a component range of 14 wt% to 16 wt%, V in a component range of 10 wt% to 12 wt%, and a component range of 0.003 wt% to 0.01 wt% A Ni-based alloy consisting of B and the balance Ni, and having a dual-phase structure having a phase composed of an intermetallic compound of Ni and Al and a phase composed of an intermetallic compound of Ni and V. Provided with a probe that can enter the parts to be processed during friction stir welding,
The friction stir welding tool including the Ni-based alloy according to claim 1.   The friction stir welding tool according to claim 2, wherein the probe has a probe main body and a tip layer laminated on the probe main body, and the tip layer is made of the Ni-based alloy.   4. The friction stir welding tool according to claim 2, wherein the tip layer is a portion that intrudes into the processing target component during the friction stir welding. Al in a component range of 2 wt% to 4 wt%, Ta in a component range of 14 wt% to 16 wt%, V in a component range of 10 wt% to 12 wt%, and a component range of 0.003 wt% to 0.01 wt% Preparing a raw metal powder comprising B and the balance Ni;
A nozzle member of a laser deposition apparatus capable of mixing the raw metal powder into a carrier gas and ejecting it to the end of the main body member and irradiating laser light to the end of the main body member, A step of disposing it facing the end,
The step of moving the nozzle member along the end of the body member while irradiating the laser beam while ejecting the raw metal powder from the nozzle member;
After the step of moving the nozzle member along the end of the body member is completed, a solution treatment is performed on the built-up layer of the body member;
The manufacturing method which manufactures the tool for friction stir welding in any one of Claim 2 to 4 provided with these.