阅读说明：本技术 一种提高大块非晶合金摩擦焊接效果的方法和块体非晶合金 (Method for improving friction welding effect of bulk amorphous alloy and bulk amorphous alloy ) 是由 王成勇 甄铁城 唐梓敏 王相煜 陈伟专 于 2021-08-04 设计创作，主要内容包括：本发明涉及非晶合金连接技术领域,特别是涉及一种提高大块非晶合金摩擦焊接效果的方法和大块非晶合金,该焊接成型方法包括以下步骤,S1、采用具有交叉过冷液相区温度的待焊接的第一非晶合金和第二非晶合金,在第一非晶合金的待焊接端加工出焊接头,在第二非晶合金的待焊接端加工出焊接槽；S2、将焊接头插入焊接槽,采用套筒套住所述焊接头与所述焊接槽的连接处；S3、驱动所述第一非晶合金与所述第二非晶合金做相对旋转运动,实现焊接成型；S4、重复S1～S3步骤,获得多块非晶合金,该摩擦焊接方法能够有效增大摩擦焊接的接触面积,且具有焊接均匀和焊接效率高的优点。(The invention relates to the technical field of amorphous alloy connection, in particular to a method for improving the friction welding effect of a massive amorphous alloy and the massive amorphous alloy, wherein the welding forming method comprises the following steps of S1, adopting a first amorphous alloy and a second amorphous alloy which have cross supercooled liquid region temperature and are to be welded, processing a welding head at the end to be welded of the first amorphous alloy, and processing a welding groove at the end to be welded of the second amorphous alloy; s2, inserting a welding head into the welding groove, and sheathing the joint of the welding head and the welding groove by a sleeve; s3, driving the first amorphous alloy and the second amorphous alloy to do relative rotation movement, and realizing welding forming; s4, repeating the steps S1-S3 to obtain a plurality of amorphous alloys, wherein the friction welding method can effectively increase the contact area of friction welding and has the advantages of uniform welding and high welding efficiency.)

1. A method for improving the friction welding effect of a massive amorphous alloy is characterized in that: comprises the following steps of (a) carrying out,

s1, adopting a first amorphous alloy and a second amorphous alloy which have cross supercooled liquid region temperature and are to be welded, processing a welding head at the end to be welded of the first amorphous alloy, and processing a welding groove at the end to be welded of the second amorphous alloy;

s2, inserting the welding head of the first amorphous alloy into the welding groove of the second amorphous alloy to enable the welding head to contact with the welding groove, and sheathing the joint of the welding head and the welding groove by using a sleeve;

s3, driving the first amorphous alloy and the second amorphous alloy to do relative rotation movement, and realizing welding forming of the first amorphous alloy and the second amorphous alloy;

and S4, repeating the steps S1-S3 to obtain a plurality of amorphous alloys.

2. The method for improving the friction welding effect of the bulk amorphous alloy according to claim 1, wherein the method comprises the following steps: the welding heads are a V-shaped welding head, a convex welding head, a spherical welding head and a circular truncated cone welding head with a step structure on the surface.

3. The method for improving the friction welding effect of the bulk amorphous alloy according to claim 2, wherein: and processing a microstructure with any one or two sizes of micron and nanometer on the welding head and/or the welding groove.

4. The method for improving the friction welding effect of the bulk amorphous alloy according to claim 1, wherein the method comprises the following steps: the inner wall of the sleeve is provided with a die cavity structure.

5. The method for improving the friction welding effect of the bulk amorphous alloy according to claim 1, wherein the method comprises the following steps: and a temperature measuring module is arranged above the sleeve and is used for detecting the temperature change of the welding area in real time.

6. The method for improving the friction welding effect of the bulk amorphous alloy according to claim 1, wherein the method comprises the following steps: the ultrasonic welding system applies ultrasonic vibration to the first amorphous alloy and the second amorphous alloy respectively.

7. The method for improving the friction welding effect of the bulk amorphous alloy according to claim 6, wherein the method comprises the following steps: in S3, the ultrasonic welding system applies pressure to the first amorphous alloy and/or the second amorphous alloy, so that the end to be welded of the first amorphous alloy and the end to be welded of the second amorphous alloy are pressed together.

8. The method for improving the friction welding effect of the bulk amorphous alloy according to claim 7, wherein the method comprises the following steps: the vibration power of the ultrasonic vibration is not more than 2kW, and the pressure of the pressure is not more than 5 GPa.

9. The method for improving the friction welding effect of the bulk amorphous alloy according to claim 1, wherein the method comprises the following steps: the relative rotation motion of the first amorphous alloy and/or the second amorphous alloy is a main motion, and the rotation speed of the main motion is not more than 1500 rpm.

10. A bulk amorphous alloy, characterized by: is manufactured by the friction welding method for the bulk amorphous alloy according to any one of claims 1 to 9.

Technical Field

The invention relates to the technical field of amorphous alloy connection, in particular to a method for improving the friction welding effect of a bulk amorphous alloy and the bulk amorphous alloy.

Background

The amorphous alloy is used as a novel high-performance metal material, and has excellent high strength, high hardness, high elastic modulus and good wear resistance and corrosion resistance, so that the amorphous alloy plays a certain supporting role in the fields of military industry, electronics, aerospace and the like. At present, the size of the amorphous alloy is limited to centimeter level, and the amorphous alloy in the decimetric level is very little, so that the application of the amorphous alloy in the industry is greatly limited, which seriously limits the popularization of the amorphous alloy in various application fields.

The amorphous alloy can generate superplastic rheology in the supercooled liquid region, and the amorphous alloy always keeps an amorphous state when the amorphous alloy works in the temperature range. Therefore, the amorphous alloy can be welded and formed into a large-size amorphous alloy by utilizing the superplastic rheological behavior of the amorphous alloy in the supercooled liquid region.

The rotary friction welding is one of the most common means for metal welding process, and utilizes the friction heat generated by the rotation of two welding materials and the plastic deformation capacity thereof to raise the temperature of the welding friction surface to a high-temperature plastic state, thereby realizing the solid connection of the two materials. The rotary friction welding has the characteristics of simple process and high efficiency, but the rotary friction welding has short stroke, narrow welding diffusion reaction layer, uneven heat generated at a welding interface and general welding effect, and the performance of the material obtained after welding cannot be ensured.

Currently, for example, patent No. cn2006101615937.x discloses a processing method of spin friction welding. According to the method, annular slag receiving grooves are formed in a first part and a second part to be welded in advance, the groove wall close to a friction welding surface is higher, the first part and the second part are in relative rotary contact and friction extrusion along the axial direction in the rotary friction welding process, high temperature is generated to enable the slag receiving grooves to be molten and sealed, slag leakage can be effectively reduced, and pollution caused by falling of slag is avoided.

For example, patent CN201611030626.2 discloses a sheath structure for friction welding of dissimilar metals and a friction welding method, in the process of the friction welding, the end of a titanium or titanium alloy rod with external threads is in threaded connection with the sheath structure with internal threads, and the end face of a steel rod and the end face of a steel material of the sheath structure are in contact friction with each other, so as to finally realize solid connection of two dissimilar metals. The method can reduce the residual stress of the welding area and thoroughly remove the oxide on the surface of the steel, and meanwhile, the sheath structure can play a role in restraining metal by the mold, so that the welding quality is improved. However, the method causes the friction deformation layer to move to one side of the steel, the quality of a welding joint is poor, the mechanical property and the service performance of a product are affected, meanwhile, different sheath structures need to be designed aiming at different materials with different shapes, sizes and types, and the production cost is increased.

For example, Shin HS et Al, "ionization welding of Zr55Al10Ni5Cu30 bulk metallic glasses, Shin HS, Jeong YJ, Choi HY, et Al, Materials transformations, 2005,46(12): 2768-2772" discloses a novel Friction welding device, which is equipped with a pneumatic actuator and a clamp on the basis of a common lathe, can accurately control Friction time and Friction force, realizes rotary Friction welding of Zr-based bulk amorphous alloy, does not have obvious pores or cracks on an amorphous alloy interface obtained by the device, and can realize Friction welding without crystallization, but the device has a complex structure and complicated operation steps, is not beneficial to repeated operation, and has protrusions on the amorphous alloy surface obtained after welding, and the overall shape quality of the material is poor, and is not beneficial to commercial use.

Therefore, the friction connection mode of the existing amorphous alloy still has the following defects: the spin friction welding has the characteristics of short stroke, high welding efficiency and the like, but the diffusion welding reaction layer is narrow, the heat distribution of a welding interface is uneven, the welding effect is difficult to ensure, for example, in the spin friction welding process of the amorphous alloy, the welding is uneven or insufficient due to the problems of uneven heat distribution and the like, and the welding effect is poor; in the process of rotating friction welding of the same amorphous alloy or different amorphous alloys, the temperature changes rapidly, if the temperature is too high, the amorphous alloy is crystallized, even a welding interface is melted, and for the condition of obtaining the temperature change of a welding area in time, the crystallization of the amorphous alloy is prevented from being one of important concerns in the amorphous welding process; in the friction welding process of the amorphous alloy, burrs or flashes are easy to appear on a welding interface, even some interface regions deform, the joint strength is low, and the shape quality of a product is poor.

Disclosure of Invention

The invention aims to overcome the defects in the prior art and provide the method for improving the friction welding effect of the bulk amorphous alloy.

The purpose of the invention is realized by the following technical scheme:

provides a method for improving the friction welding effect of bulk amorphous alloy, which comprises the following steps,

s1, adopting a first amorphous alloy and a second amorphous alloy which have cross supercooled liquid region temperature and are to be welded, processing a welding head at the end to be welded of the first amorphous alloy, and processing a welding groove at the end to be welded of the second amorphous alloy;

s2, inserting the welding head of the first amorphous alloy into the welding groove of the second amorphous alloy to enable the welding head to contact with the welding groove, and sheathing the joint of the welding head and the welding groove by using a sleeve;

s3, driving the first amorphous alloy and the second amorphous alloy to do relative rotation movement, and realizing welding forming of the first amorphous alloy and the second amorphous alloy;

and S4, repeating the steps S1-S3 to obtain a plurality of amorphous alloys.

The working principle of the steps is as follows:

a welding head is machined at the end to be welded of the first amorphous alloy, a welding groove is machined at the end to be welded of the second amorphous alloy, and the welding head and the welding groove are mutually sleeved, so that the welding contact interface area of the first amorphous alloy and the second amorphous alloy is effectively increased, the heat generated by rotary friction welding is favorably improved, the dispersion uniformity of the heat is improved, and the welding efficiency is improved.

Further, the welding heads are a V-shaped welding head, a convex welding head, a spherical welding head and a circular truncated cone welding head with a step structure on the surface.

Further, a microstructure with any one or a combination of two sizes of micron-scale and nanometer-scale is processed on the welding head and/or the welding groove. The microstructure further increases the welding contact area and the surface roughness, is favorable for improving the heat generated by the rotary friction welding, and improves the welding efficiency.

Furthermore, the sleeve is used for limiting the joint of the first amorphous alloy and the second amorphous alloy, preventing the amorphous alloy from deforming in the welding process, reducing the generation of flash or burr and obtaining a large amorphous alloy with better shape and quality.

Further, the inner wall of the sleeve is provided with a die cavity structure, and the die cavity structure does not react with the first amorphous alloy and the second amorphous alloy in the welding process. The inner wall of the sleeve is of a die cavity structure, so that the amorphous alloy is shaped into a required shape in the welding forming process, and the functionality of an amorphous alloy product is improved.

Furthermore, a temperature measuring module is arranged above the sleeve. The temperature measurement module is used for detecting the temperature of a welding joint and can obtain the temperature change of an amorphous alloy welding area in real time, so that the welding process is adjusted in real time, and the problem that the amorphous alloy is crystallized or cannot be welded due to too low temperature caused by too high welding temperature is solved.

Further, the ultrasonic welding system is further included, and the ultrasonic welding system applies ultrasonic vibration to the first amorphous alloy and the second amorphous alloy respectively. The ultrasonic vibration is beneficial to reducing the nonuniformity of heat distribution of a welding interface, improving the heat exchange efficiency in the welding process and obtaining better welding effect.

Further, the ultrasonic welding system applies pressure to the first amorphous alloy and/or the second amorphous alloy, so that the end to be welded of the first amorphous alloy and the end to be welded of the second amorphous alloy are pressed together.

Further, the vibration power of the ultrasonic vibration is not more than 2kW, and the pressure magnitude of the pressure is not more than 5 GPa.

Further, the relative rotation motion of the first amorphous alloy and/or the second amorphous alloy is a main motion, main motion parameters of the first amorphous alloy and the second amorphous alloy are respectively set, and the rotation speed of the main motion is not more than 1500 rpm.

The method for improving the friction welding effect of the bulk amorphous alloy has the beneficial effects that:

(1) according to the invention, the welding head is processed at the end to be welded of the first amorphous alloy, and the welding groove is processed at the end to be welded of the second amorphous alloy, so that the contact area of the welding interface of the first amorphous alloy and the second amorphous alloy is effectively increased, the heat generated by the rotary friction welding is favorably improved, the heat exchange efficiency is improved, the welding efficiency is further improved, and meanwhile, the phenomena of uneven welding or insufficient welding and the like caused by uneven heat distribution of the amorphous alloy in the welding process are effectively avoided.

(2) The sleeve is used for limiting the joint of the first amorphous alloy and the second amorphous alloy, preventing the welding part of the amorphous alloy from deforming, reducing the generation of fins or burrs and obtaining the bulk amorphous alloy with better shape and quality.

The invention also provides a bulk amorphous alloy which is prepared by adopting the friction welding method for the bulk amorphous alloy.

Drawings

The invention is further illustrated by means of the attached drawings, but the embodiments in the drawings do not constitute any limitation to the invention, and for a person skilled in the art, other drawings can be derived on the basis of the following drawings without inventive effort.

Fig. 1 is a schematic view of an operating state of an amorphous alloy friction welding system of example 1.

Fig. 2 is a schematic view of the working state of the amorphous alloy friction welding system of example 2.

FIG. 3 is a schematic view showing the operation state of the amorphous alloy friction welding system of example 3.

FIG. 4 is a schematic view showing the operation state of the amorphous alloy friction welding system of example 4.

FIG. 5 is a schematic view showing the operation state of the amorphous alloy friction welding system of example 5.

FIG. 6 is a schematic view showing the operation state of the amorphous alloy friction welding system of example 6.

Reference numerals:

a first amorphous alloy 1; a second amorphous alloy 2; an ultrasonic welding system 3; a sleeve 4; a temperature measuring module 5; bulk amorphous alloy 6; a microstructure 7; a gear shape 8.

Detailed Description

The invention is further described with reference to the following examples and the accompanying drawings.

Example 1

The method for improving the friction welding effect of the bulk amorphous alloy disclosed in the present example is shown in figure 1,

s1, selecting amorphous alloys with the components of Zr41.2Ti13.8Cu12.5Ni10Be22.5 as a first amorphous alloy 1 and a second amorphous alloy 2 according to welding requirements, wherein the Tg of the amorphous alloys is 365 ℃, the Tx of the amorphous alloys is 419 ℃, simultaneously processing the end to be welded of the first amorphous alloy 1 into a V-shaped welding head by adopting a laser processing mode, processing the end to be welded of the second amorphous alloy 2 into a V-shaped welding groove, and controlling the temperature range of the cross supercooling liquid phase region of the first amorphous alloy 1 and the second amorphous alloy 2 to be 365-419 ℃.

S2, clamping the first amorphous alloy 1 and the second amorphous alloy 2 on the ultrasonic welding system 3, inserting the welding head of the first amorphous alloy 1 into the welding groove of the second amorphous alloy 2, and sleeving the joint of the welding head and the welding groove by using the sleeve 4 to enable interfaces to be welded to be in contact with each other.

S3, setting the main rotation motion of the first amorphous alloy 1 to rotate anticlockwise along the axial relative motion direction, wherein the rotation speed is 250rpm, the main rotation motion of the second amorphous alloy 2 is opposite to the main rotation motion direction of the first amorphous alloy 1, and the rotation speed is 250 rpm; setting ultrasonic power of 500W, outputting ultrasonic vibration along the axial relative motion direction, and ensuring that the first amorphous alloy 1 and the second amorphous alloy 2 do relative translational motion along the axial direction by pressure so as to enable interfaces to be welded to rub and extrude with each other; setting the measurement temperature range to be 355-429 ℃ according to the temperature range of the cross supercooling liquid phase region. And starting the ultrasonic welding system 3, enabling the first amorphous alloy 1 and the second amorphous alloy 2 to do relative rotation movement, and ensuring that friction welding is completed in the crossed supercooled liquid region by acquiring the temperature change condition of the welding region in real time to obtain the bulk amorphous alloy 6.

And S4, circularly operating, and repeating the steps S1-S3 to obtain a plurality of amorphous alloys.

Example 2

The method for improving the friction welding effect of the bulk amorphous alloy disclosed in the present example is shown in fig. 2,

s1, according to welding requirements, selecting amorphous alloys with the components of Pd47Ni10Cu30P13 as a first amorphous alloy 1 and a second amorphous alloy 2, wherein Tg is 354 ℃, Tx is 400 ℃, simultaneously processing the end to be welded of the first amorphous alloy 1 into a spherical welding joint by adopting a laser processing mode, processing the end to be welded of the second amorphous alloy 2 into a spherical welding groove, and controlling the temperature range of the cross supercooling liquid phase region of the first amorphous alloy 1 and the second amorphous alloy 2 to be 354-400 ℃.

S2, clamping the first amorphous alloy 1 and the second amorphous alloy 2 on the ultrasonic welding system 3, inserting the welding head of the first amorphous alloy 1 into the welding groove of the second amorphous alloy 2, and sleeving the joint of the welding head and the welding groove by using the sleeve 4 to enable interfaces to be welded to be in contact with each other.

S3, setting the main rotation motion of the first amorphous alloy 1 to rotate anticlockwise along the axial relative motion direction, wherein the rotation speed is 500rpm, and the main rotation motion of the second amorphous alloy 2 is opposite to the main rotation motion direction of the first amorphous alloy 1 and the rotation speed is 250 rpm; setting ultrasonic power of 500W, outputting ultrasonic vibration along the axial relative motion direction, and ensuring that the first amorphous alloy 1 and the second amorphous alloy 2 do relative translational motion along the axial direction by pressure so as to enable interfaces to be welded to rub and extrude with each other; setting the measurement temperature range to be 344-410 ℃ according to the temperature range of the cross supercooling liquid phase region. And starting the ultrasonic welding system 3, enabling the first amorphous alloy 1 and the second amorphous alloy 2 to do relative rotation movement, and ensuring that friction welding is completed in the crossed supercooled liquid region by acquiring the temperature change condition of the welding region in real time to obtain the bulk amorphous alloy 6.

And S4, circularly operating, and repeating the steps S1-S3 to obtain a plurality of amorphous alloys.

Example 3

The method for improving the friction welding effect of the bulk amorphous alloy disclosed in the present example is shown in fig. 3,

s1, selecting amorphous alloys with the components of Zr37Al10Cu11.25Ti12.5Be20.25 as a first amorphous alloy 1 and a second amorphous alloy 2 according to welding requirements, wherein Tg is 360 ℃, Tx is 427 ℃, simultaneously processing the end to be welded of the first amorphous alloy 1 into a V-shaped welding head by adopting an ultrasonic processing mode, processing the end to be welded of the second amorphous alloy 2 into a V-shaped welding groove, processing the microstructure 7 at the end to be welded by adopting a laser processing mode, and controlling the temperature range of the cross supercooling liquid phase region of the first amorphous alloy 1 and the second amorphous alloy 2 to be 360-427 ℃.

S2, clamping the first amorphous alloy 1 and the second amorphous alloy 2 on the ultrasonic welding system 3, inserting the welding head of the first amorphous alloy 1 into the welding groove of the second amorphous alloy 2, and sleeving the joint of the welding head and the welding groove by using the sleeve 4 to enable interfaces to be welded to be in contact with each other.

S3, setting the main rotation motion of the first amorphous alloy 1 to rotate anticlockwise along the axial relative motion direction, wherein the rotation speed is 500rpm, the main rotation motion of the second amorphous alloy 2 is opposite to the main rotation motion direction of the first amorphous alloy 1, and the rotation speed is 0 rpm; setting the ultrasonic power to be 0W, and ensuring that the first amorphous alloy 1 and the second amorphous alloy 2 do relative translational motion along the axial direction by pressure so as to enable interfaces to be welded to be mutually rubbed and extruded; setting the measurement temperature range to 350-437 ℃ according to the temperature range of the cross supercooling liquid phase region. And starting the ultrasonic welding system 3, enabling the first amorphous alloy 1 and the second amorphous alloy 2 to do relative rotation movement, and ensuring that friction welding is completed in the crossed supercooled liquid region by acquiring the temperature change condition of the welding region in real time to obtain the bulk amorphous alloy 6.

And S4, circularly operating, and repeating the steps S1-S3 to obtain a plurality of amorphous alloys.

Example 4

The method for improving the friction welding effect of the bulk amorphous alloy disclosed in the present example is shown in fig. 4,

s1, according to welding requirements, selecting an amorphous alloy with the components of Zr41.2Ti13.8Cu12.5Ni10Be22.5 as a first amorphous alloy 1, wherein the Tg is 365 ℃, the Tx is 419 ℃, selecting an amorphous alloy with the components of Zr37Al10Cu11.25Ti12.5Be20.25 as a second amorphous alloy 2, wherein the Tg is 360 ℃, and the Tx is 427 ℃, simultaneously processing a welding end of the first amorphous alloy 1 into a V-shaped welding head in a milling mode, processing a to-be-welded end of the second amorphous alloy 2 into a V-shaped welding groove, processing microstructures 7 at the to-be-welded end in a laser processing mode, and setting the temperature range of a cross liquid phase region of the first amorphous alloy 1 and the second amorphous alloy 2 to be 365-419 ℃.

S2, clamping the first amorphous alloy 1 and the second amorphous alloy 2 on the ultrasonic welding system 3, inserting the welding head of the first amorphous alloy 1 into the welding groove of the second amorphous alloy 2, and sleeving the joint of the welding head and the welding groove by using the sleeve 4 to enable interfaces to be welded to be in contact with each other.

S3, setting the main rotation motion of the first amorphous alloy 1 to rotate anticlockwise along the axial relative motion direction, wherein the rotation speed is 250rpm, the main rotation motion of the second amorphous alloy 2 is opposite to the main rotation motion direction of the first amorphous alloy 1, and the rotation speed is 0 rpm; setting ultrasonic power of 500W, outputting ultrasonic vibration along the axial relative motion direction, and ensuring that the first amorphous alloy 1 and the second amorphous alloy 2 do relative translational motion along the axial direction by pressure so as to enable interfaces to be welded to rub and extrude with each other; setting the measurement temperature range to be 355-429 ℃ according to the temperature range of the cross supercooling liquid phase region. And starting the ultrasonic welding system 3, enabling the first amorphous alloy 1 and the second amorphous alloy 2 to do relative rotation movement, and ensuring that friction welding is completed in the crossed supercooled liquid region by acquiring the temperature change condition of the welding region in real time to obtain the bulk amorphous alloy 6.

And S4, circularly operating, and repeating the steps S1-S3 to obtain a plurality of amorphous alloys.

Example 5

The method for improving the friction welding effect of the bulk amorphous alloy disclosed in the present example is shown in fig. 5,

s1, selecting amorphous alloys with the components of Zr41.2Ti13.8Cu12.5Ni10Be22.5 as a first amorphous alloy 1 and a second amorphous alloy 2 according to welding requirements, wherein Tg is 365 ℃, Tx is 419 ℃, simultaneously processing the end to be welded of the first amorphous alloy 1 into a V-shaped welding head by adopting a laser processing mode, processing the end to be welded of the second amorphous alloy 2 into a V-shaped welding groove, processing the microstructure 7 at the end to be welded by adopting an ultrasonic processing mode, and controlling the temperature range of the supercooling liquid phase region of the first amorphous alloy 1 and the supercooling liquid phase region of the second amorphous alloy 2 to be 365-419 ℃.

S2, clamping the first amorphous alloy 1 and the second amorphous alloy 2 on the ultrasonic welding system 3, wherein the welding head of the first amorphous alloy 1 is inserted into the welding groove of the second amorphous alloy 2, and the interfaces to be welded are in contact with each other.

S3, setting the main rotation motion of the first amorphous alloy 1 to rotate anticlockwise along the axial relative motion direction, wherein the rotation speed is 250rpm, the main rotation motion of the second amorphous alloy 2 is opposite to the main rotation motion direction of the first amorphous alloy 1, and the rotation speed is 250 rpm; setting ultrasonic power of 500W, outputting ultrasonic vibration along the axial relative motion direction, and ensuring that the first amorphous alloy 1 and the second amorphous alloy 2 do relative translational motion along the axial direction by pressure so as to enable interfaces to be welded to rub and extrude with each other; setting the measurement temperature range to be 355-429 ℃ according to the temperature range of the cross supercooling liquid phase region. And starting the ultrasonic welding system 3, enabling the first amorphous alloy 1 and the second amorphous alloy 2 to do relative rotation movement, and ensuring that friction welding is completed in the crossed supercooled liquid region by acquiring the temperature change condition of the welding region in real time to obtain the bulk amorphous alloy 6.

And S4, circularly operating, and repeating the steps S1-S3 to obtain a plurality of amorphous alloys.

Example 6

The method for improving the friction welding effect of the bulk amorphous alloy disclosed in the present example is shown in fig. 6,

s1, selecting amorphous alloys with the components of Zr41.2Ti13.8Cu12.5Ni10Be22.5 as a first amorphous alloy 1 and a second amorphous alloy 2 according to welding requirements, wherein Tg is 365 ℃, Tx is 419 ℃, simultaneously processing the end to be welded of the first amorphous alloy 1 into a V-shaped welding head by adopting a laser processing mode, processing the end to be welded of the second amorphous alloy 2 into a V-shaped welding groove, processing the microstructure 7 at the end to be welded by adopting the laser processing mode, and controlling the temperature range of the supercooling liquid phase region of the first amorphous alloy 1 and the supercooling liquid phase region of the second amorphous alloy 2 to be 365-419 ℃.

S2, clamping the first amorphous alloy 1 and the second amorphous alloy 2 on the ultrasonic welding system 3, wherein a welding head of the first amorphous alloy 1 is inserted into a welding groove of the second amorphous alloy 2, the joint of the welding head and the welding groove is sleeved by a sleeve 4, so that interfaces to be welded of the welding head and the welding groove are in mutual contact, and the inner wall of the sleeve 4 is a gear-shaped 8 die cavity.

S3, setting the main rotation motion of the first amorphous alloy 1 to rotate anticlockwise along the axial relative motion direction, wherein the rotation speed is 250rpm, the main rotation motion of the second amorphous alloy 2 is opposite to the main rotation motion direction of the first amorphous alloy 1, and the rotation speed is 250 rpm; setting ultrasonic power of 500W, outputting ultrasonic vibration along the axial relative motion direction, and ensuring that the first amorphous alloy 1 and the second amorphous alloy 2 do relative translational motion along the axial direction by pressure so as to enable interfaces to be welded to rub and extrude with each other; setting the measurement temperature range to be 355-429 ℃ according to the temperature range of the cross supercooling liquid phase region. And starting the ultrasonic welding system 3, enabling the first amorphous alloy 1 and the second amorphous alloy 2 to do relative rotation movement, and ensuring that friction welding is finished in the crossed supercooled liquid region by acquiring the temperature change condition of the welding region in real time to obtain the massive amorphous alloy 6 with the gear structure.

And S4, circularly operating, and repeating the steps S1-S3 to obtain a plurality of amorphous alloys.

Finally, it should be noted that the above embodiments are only used for illustrating the technical solutions of the present invention, and not for limiting the protection scope of the present invention, although the present invention is described in detail with reference to the preferred embodiments, it should be understood by those skilled in the art that modifications or equivalent substitutions can be made on the technical solutions of the present invention without departing from the spirit and scope of the technical solutions of the present invention.