阅读说明：本技术 高强度钢的焊缝处理方法及系统 (Welding seam processing method and system for high-strength steel ) 是由 肖彪 李翔 贾冬梅 彭群峰 许晓刚 魏敏君 周焕能 钟真 吴盛祥 于 2021-10-18 设计创作，主要内容包括：本发明公开一种高强度钢的焊缝处理方法及系统,其中,所述高强度钢的焊缝处理方法包括：提供待焊接的部件,其中所述部件的材料为高强度钢；对所述部件进行焊接；以及对所述部件的焊缝进行至少两次激光热处理,以获得回火马氏体组织。所述高强度钢的焊缝处理系统包括安装在同一机床上的保护气体装置、焊接装置和至少一个激光处理装置,其中,所述至少一个激光处理装置用于对所述部件的焊缝进行至少两次激光热处理。本发明可以实现高效、高精度、高质量的焊缝软化热处理技术方案,可降低焊缝断裂风险,避免因焊缝韧性过低、氢脆或焊缝硬度过高导致各种形式的焊缝断裂问题。(The invention discloses a method and a system for processing a welding seam of high-strength steel, wherein the method for processing the welding seam of the high-strength steel comprises the following steps: providing a part to be welded, wherein the material of the part is high strength steel; welding the components; and performing at least two laser heat treatments on the weld of the component to obtain a tempered martensite structure. The system for processing the welding seam of the high-strength steel comprises a shielding gas device, a welding device and at least one laser processing device which are arranged on the same machine tool, wherein the at least one laser processing device is used for carrying out laser heat treatment on the welding seam of the part at least twice. The invention can realize the technical scheme of softening heat treatment of the welding seam with high efficiency, high precision and high quality, can reduce the fracture risk of the welding seam, and avoids the fracture problems of various forms of welding seams caused by over-low toughness, hydrogen embrittlement or over-high hardness of the welding seam.)

1. A method for processing a weld of high-strength steel, comprising:

providing a part to be welded, wherein the material of the part is high strength steel;

welding the components; and

the weld of the component is subjected to at least two laser heat treatments to obtain a tempered martensitic structure.

2. The method for processing the weld of the high-strength steel according to claim 1, wherein the high-strength steel is a high-strength steel having a tensile strength of not less than 900MPa after water-cooling quenching.

3. The method for processing a weld of high strength steel according to claim 1, wherein the welding is selected from one of laser tailor welding, resistance spot welding, and arc welding.

4. The method for processing a weld of high strength steel according to claim 1, wherein the laser heat treatment is a segmented laser heat treatment to achieve precise control of the metallographic structure transformation of the weld.

5. The method for processing a weld of high strength steel according to claim 1, wherein the first laser heat treatment of the at least two laser heat treatments is started within 0 to 2 minutes after the welding is completed.

6. The method for processing a weld of high strength steel according to claim 1, wherein the weld after at least two laser heat treatments sequentially forms a first layer of tempered martensite structure, a ferrite and martensite dual-phase structure, and a second layer of tempered martensite structure from the surface to the inside.

7. The method for processing a weld of high strength steel according to claim 6, wherein a martensite structure is further formed between the first tempered martensite structure and the ferrite-martensite dual phase structure.

8. A weld processing system for high strength steel, comprising:

a shielding gas device for providing shielding gas;

the welding device is used for welding a part to be welded under the protective gas atmosphere, wherein the part is made of high-strength steel; and

at least one laser treatment device for performing at least two laser heat treatments on the weld of the component to obtain a tempered martensitic structure;

wherein the shielding gas device, the welding device and the at least one laser processing device are mounted on the same machine tool.

9. The high strength steel weld processing system of claim 8, further comprising: the protective gas device, the welding device, the at least one laser processing device and the non-contact temperature measuring device are respectively connected with the computer, the non-contact temperature measuring device is used for continuously measuring the temperature of the surface of the welding seam, and the computer is used for realizing power feedback control of the laser heat treatment according to the temperature of the surface of the welding seam and the process data of the laser heat treatment.

10. The high strength steel weld processing system of claim 8, wherein the welding device is a laser welding device that shares a laser source with the at least one laser processing device.

Technical Field

The invention relates to the technical field of steel welding seam processing, in particular to a welding seam processing method and system for high-strength steel.

Background

At present, after materials containing higher alloy elements are welded by means of resistance spot welding, arc welding, oxygen arc welding, laser tailor welding and the like, a welding seam has a large amount of quenching structures because the welding seam is influenced by nearby cold base materials in a molten high-temperature state. The martensite content in the welding seam is high, so that the plasticity of the welding seam is poor, and the problems of delayed cracking, fracture of a welding seam area, fatigue fracture, micro stress concentration fracture and the like of the welding seam are caused. On one hand, in the production activity, the fracture of the welding line can cause great loss or safety accidents to the production rhythm of an enterprise; on the other hand, during use by the consumer, the weld breaks, which may result in casualties. Such problems severely restrict the development, production and use of this part of the material. Taking laser tailor-welding of automobile parts as an example, after tailor-welding, if the martensite of the welding seam is too much and the hardness is too high, the high-strength steel can cause the fracture problems of different forms such as delayed fracture, fatigue fracture, impact fracture and the like caused by hydrogen of the welding seam.

In order to reduce the brittleness of the welding seam and improve the plasticity of the welding seam, the electromagnetic induction heat treatment, the flame heat treatment, the electric radiant tube heat treatment and other technical schemes are provided at present. The electromagnetic induction heat treatment technology is mature, and has more advantages, including the advantages of heat treatment and rapid heat treatment of parts with large thickness, low cost and the like. The laser surface quenching technology has more heat treatment on the surface of a part, can cause the phenomena of surface quenching and back tempering of the part, and is also applied to the technologies of surface tempering, annealing and the like of the laser.

However, the electromagnetic induction heat treatment device is large, the requirement on the heat treatment distance is strict, the electromagnetic induction heat treatment device cannot be normally installed and moved or can form enough heat effect locally under the condition of limited space, meanwhile, the magnetic induction lines adopted by the electromagnetic induction heat treatment can be dispersed and are not controlled, the heat treatment range is not accurately controlled, the electromagnetic induction heat treatment device is not suitable for local tempering of welding seams, the temperature control precision of the electromagnetic induction heat treatment is not high enough, and the electromagnetic induction heat treatment device is not suitable for heat treatment of welding seams and welding spots with complicated part structures and distributed dispersedly. The flame heat treatment technology has great safety problem, the heat treatment range is not easy to control, the efficiency is low, the appearance of the part is influenced, and the supporting equipment is damaged. The working efficiency of the electric radiant tube is not high, and the position of a welding line is generally required to be sent into the radiant furnace and cannot be locally controlled.

The existing laser surface quenching technology can not solve the internal martensite tempering requirement of high-strength steel, even increases the surface hardening degree of the material, so that the surface delayed cracking risk is greatly increased, and the case that the laser surface quenching technology is applied to weld heat treatment is not available. And the laser surface quenching technology is only adopted, although the interior of the part has a certain tempering effect, the quality requirement on the welding seam is far from enough. Most of the laser surface quenching technology is applied to semiconductor materials, and has no guiding significance on the processing of welding seams. In addition, the tempering heat quantity of the laser surface quenching technology is too small to meet the internal tempering requirement of the component. Generally, the laser surface quenching technology is advanced, but no deep research is carried out in the laser surface quenching technology and the work of reducing delayed cracking of welding seams by utilizing the laser surface quenching technology.

Therefore, it is urgently needed to provide a method and a system for processing a weld of high-strength steel to solve the above technical problems.

Disclosure of Invention

The invention mainly aims to provide a method and a system for processing a welding seam of high-strength steel, and aims to solve the problem of welding seam fracture in various forms caused by too low toughness, hydrogen embrittlement or too high hardness of the welding seam.

In order to achieve the above object, the present invention provides a method for processing a weld of high strength steel, comprising: providing a part to be welded, wherein the material of the part is high strength steel; welding the components; and performing at least two laser heat treatments on the weld of the component to obtain a tempered martensite structure.

Preferably, the high-strength steel is high-strength steel with the tensile strength of more than or equal to 900MPa after water-cooling quenching.

Preferably, the welding is selected from one of laser tailor welding, resistance spot welding, arc welding.

Preferably, the laser heat treatment is a segmented laser heat treatment to achieve precise control of the metallographic structure transformation of the weld.

Preferably, the first of the at least two laser heat treatments is started 0 to 2 minutes after the welding is completed.

Preferably, the weld joint after at least two laser heat treatments sequentially forms a first layer of tempered martensite structure, a ferrite and martensite dual-phase structure and a second layer of tempered martensite structure from the surface to the inside.

Preferably, a martensite structure may be further formed between the first tempered martensite structure and the ferrite-martensite dual phase structure. And other minor amounts of bainite, sorbite, and the like.

In order to achieve the above object, the present invention further provides a system for processing a weld of high strength steel, including: a shielding gas device for providing shielding gas; the welding device is used for welding a part to be welded under the protective gas atmosphere, wherein the part is made of high-strength steel; and at least one laser treatment device for performing at least two laser heat treatments on the weld of the component to obtain a tempered martensitic structure; wherein the shielding gas device, the welding device and the at least one laser processing device are mounted on the same machine tool. The protective gas is non-oxidizing gas such as high-purity nitrogen, helium or mixed gas, and at least meets the dew point of the protective gas below 10 ℃, and the preferred dew point is below-10 ℃.

Preferably, the weld processing system for high strength steel further includes: the protective gas device, the welding device, the at least one laser processing device and the non-contact temperature measuring device are respectively connected with the computer, the non-contact temperature measuring device is used for continuously measuring the temperature of the surface of the welding seam, and the computer is used for realizing power feedback control of the laser heat treatment according to the temperature of the surface of the welding seam and the process data of the laser heat treatment.

Preferably, the welding device is a laser welding device that shares a laser source with the at least one laser processing device.

According to the method and the system for processing the high-strength steel welding line, the tempered martensite structure is obtained by performing laser heat treatment on the welding line for at least two times after welding, so that the technical scheme of softening heat treatment of the welding line with high efficiency, high precision and high quality can be realized, and the risk of fracture of the welding line can be reduced.

After the two laser heat treatments, namely the first laser heat treatment on the welding line, the welding line is air-cooled or air-cooled, and due to the higher heat treatment temperature, the air-cooled quenching phenomenon appears under the action of material components, so that a surface martensite structure is formed. And carrying out laser heat treatment on the welding seam for the second time and later so as to carry out tempering treatment on the primary air-cooled quenching structure, improve the toughness of the welding seam and reduce the hardness of the welding seam.

Drawings

In order to more clearly illustrate the embodiments of the present invention or the technical solutions in the prior art, the drawings used in the description of the embodiments or the prior art will be briefly described below, it is obvious that the drawings in the following description are only some embodiments of the present invention, and for those skilled in the art, other drawings can be obtained according to the structures shown in the drawings without creative efforts.

FIG. 1 is a schematic flow diagram of a method 100 for weld treatment of high strength steel in accordance with the present invention;

FIG. 2 is a schematic diagram of a high strength steel weld processing system 200 according to the present invention;

FIG. 3 is a schematic diagram of the change in weld temperature;

FIG. 4 is a schematic structural diagram of a system for processing a weld of high strength steel according to an embodiment of the present invention;

FIG. 5 is a schematic structural diagram of a laser heating apparatus according to an embodiment of the present invention;

FIG. 6 is a schematic diagram of a scanning path of a laser spot for laser thermal processing according to an embodiment of the present invention;

FIG. 7 is a representative metallographic structure of a 1400 ℃ laser heat treated weld according to an embodiment of the present invention;

FIG. 8 is a representative layered structure diagram of a 1400 +650 laser heat treated weld joint in accordance with one embodiment of the present invention.

The implementation, functional features and advantages of the objects of the present invention will be further explained with reference to the accompanying drawings.

Detailed Description

The technical solutions in the embodiments of the present invention will be clearly and completely described below with reference to the drawings in the embodiments of the present invention, and it is obvious that the described embodiments are only a part of the embodiments of the present invention, and not all of the embodiments. All other embodiments, which can be derived by a person skilled in the art from the embodiments given herein without making any creative effort, shall fall within the protection scope of the present invention.

It should be noted that all the directional indicators (such as up, down, left, right, front, and rear … …) in the embodiment of the present invention are only used to explain the relative position relationship between the components, the movement situation, etc. in a specific posture (as shown in the drawing), and if the specific posture is changed, the directional indicator is changed accordingly.

In addition, the descriptions related to "first", "second", etc. in the present invention are only for descriptive purposes and are not to be construed as indicating or implying relative importance or implicitly indicating the number of technical features indicated. Thus, a feature defined as "first" or "second" may explicitly or implicitly include at least one such feature. In the description of the present invention, "a plurality" means at least two, e.g., two, three, etc., unless specifically limited otherwise.

In the present invention, unless otherwise expressly stated or limited, the terms "connected," "secured," and the like are to be construed broadly, and for example, "secured" may be a fixed connection, a removable connection, or an integral part; can be mechanically or electrically connected; they may be directly connected or indirectly connected through intervening media, or they may be connected internally or in any other suitable relationship, unless expressly stated otherwise. The specific meanings of the above terms in the present invention can be understood by those skilled in the art according to specific situations.

In addition, the technical solutions in the embodiments of the present invention may be combined with each other, but it must be based on the realization of those skilled in the art, and when the technical solutions are contradictory or cannot be realized, such a combination of technical solutions should not be considered to exist, and is not within the protection scope of the present invention.

The invention aims to overcome the defects of the prior art, provides a high-strength steel welding seam laser processing system and method, realizes a high-efficiency, high-precision and high-quality welding seam softening heat treatment technical scheme, can reduce the welding seam fracture risk, and avoids the problems of various forms of welding seam fracture caused by too low welding seam toughness, hydrogen embrittlement or too high welding seam hardness.

Referring to fig. 1, to achieve the above object, the present invention provides a method 100 for laser processing a weld seam of high strength steel, which mainly includes the following steps:

step S110: providing a part to be welded, wherein the material of the part is high strength steel. The high-strength steel may be, for example, high-strength steel having a tensile strength of not less than 900MPa after water-cooling quenching. The component may be, for example, steel in the form of a part, slab, strip, or the like.

Step S130: and welding the parts. The welding is, for example, one selected from laser tailor welding, resistance spot welding, and arc welding.

And step S150: the weld of the component is subjected to at least two laser heat treatments to obtain a tempered martensitic structure. In some embodiments, the laser heat treatment may be a segmented laser heat treatment, for example, to achieve precise control of the metallographic transformation of the weld. The first laser heat treatment of the at least two laser heat treatments, for example, is started within 0 to 2 minutes after the welding is completed, and the start within 30 seconds may improve the production efficiency. It should be noted that the method 100 for laser processing a weld bead of high-strength steel according to the present invention may be performed by performing the laser heat treatment on the weld bead of the member at least twice, for example, while performing the laser heat treatment on the periphery of the weld bead.

Specifically, the weld joint after at least two laser heat treatments can form a first layer of tempered martensite structure, a ferrite and martensite dual-phase structure and a second layer of tempered martensite structure from the surface to the inside in sequence.

The welding base material is a cold-rolled material, so when the laser heat treatment range covers the base material, the laser heat treatment material is distributed to the base material into a first layer of tempered martensite structure, a ferrite and martensite dual-phase structure and a second layer of cold-rolled deformation structure.

Further, a martensite structure may be formed between the first tempered martensite structure and the ferrite-martensite dual phase structure, for example. The first layer of martensite structure, ferrite and martensite dual-phase structure is formed after the first laser heat treatment, the surface temperature of the laser heat treatment exceeds 727 ℃, austenite is formed, and the structure containing martensite is formed after air cooling quenching. After the second laser heat treatment, the martensite structure in the first layer is transformed into tempered martensite.

The inventor researches and finds that the cupping values of the upper surface and the lower surface have large deviation by adopting one laser heat treatment. Generally, when the surface temperature of the first laser heat treatment is higher than 900 ℃, the cup projection value of the weld on the upper surface is lower than that on the lower surface because the martensite structure of the first heat treatment is not sufficiently tempered; when the surface temperature is lower than 1000 ℃, the cupping value of the lower surface is lower than that of the upper surface, because the lower surface obtains lower energy and the martensite in the weld of the lower surface is not sufficiently tempered. The laser heat treatment is carried out on the welding seam twice, so that the heat treatment effect can be effectively improved, and the surface martensite formed by the first laser heat treatment can be fully tempered. The measuring method of the weld joint cupping value adopts a round head cupping machine with the diameter of about 3cm, the test is stopped when visible obvious cracks appear around the weld joint, and the rising and ejecting height of the round head is the cupping value.

Referring to fig. 2, in order to achieve the above object, the present invention further provides a system 200 for processing a weld of a high strength steel, which is, for example, used to perform the method 100 for processing a weld of a high strength steel, and the working principle and details of the method 100 for processing a weld of a high strength steel are not repeated herein, please refer to the foregoing description. Only the main components thereof and the functions of the respective main components will be described below.

The high strength steel weld laser processing system 200, for example, may consist essentially of: a shielding gas device 210, a welding device 230, and at least one laser processing device 250.

The shielding gas device 210 is used, for example, to provide a shielding gas.

The welding device 230 is used, for example, for welding a component to be welded in the protective gas atmosphere, wherein the material of the component is high-strength steel.

At least one laser treatment device 250 is used, for example, to laser heat treat the weld of the component at least twice to obtain a tempered martensitic structure. It is worth mentioning here that the laser processing system 200, the at least one laser processing device 250, for example, of the high strength steel weld seam may also be used to perform the laser heat treatment on the periphery of the weld seam of the component at the same time as performing the laser heat treatment on the weld seam at least twice.

Wherein the shielding gas device 210, the welding device 230 and the at least one laser processing device 250 are mounted on the same machine tool, for example.

Further, the weld processing system 200 for high strength steel may further include, for example: a non-contact thermometry device 270 and a computer 290. The shielding gas device 210, the welding device 230, the at least one laser processing device 250, and the non-contact temperature measuring device 270 are each connected to a computer 290, for example. The non-contact thermometry device 270 is used, for example, to continuously measure the temperature of the weld surface. Computer 290 is used, for example, to implement power feedback control of the laser heat treatment based on the temperature of the weld surface and process data of the laser heat treatment.

Specifically, the welding device 230 is, for example, a laser welding device 230. The laser welding device 230 shares, for example, a laser source with at least one laser processing device 250.

The technical scheme and principle of the weld processing method and system for high-strength steel according to the present invention will be described in detail below:

after welding, laser heat treatment is carried out on the welding seam, the welding residual heat of the welding seam is utilized, meanwhile, laser heat compensation is adopted, the cooling speed is reduced, and a large amount of tempered martensite structures are obtained. After the first laser heat treatment of the welding seam, the welding seam of the component is subjected to laser heat treatment again or for multiple times, the martensite subjected to laser surface quenching is tempered, and the martensite in the welding seam is fully tempered again. Ultimately, the weld toughness can be improved, as well as the risk of hydrogen embrittlement, stress corrosion delayed cracking, and fatigue fracture of the weld.

When the temperature of the secondary laser heat treatment is in an austenite and ferrite dual-phase region, after the welding seam is cooled, a dual-phase structure of ferrite and martensite can be formed on the surface.

The sectional type laser heat treatment can be further realized by installing a plurality of laser processing devices, so that the accurate control of the transformation of the metallographic structure of the welding seam can be realized.

The technical scheme of the welding seam processing method and the welding seam processing system of the high-strength steel is mainly suitable for the high-strength steel with the tensile strength of more than or equal to 900MPa after water-cooling quenching, and the highest hardness of the welding seam area of the steel without laser annealing or tempering is generally more than or equal to 300 HV. The method has higher risks of hydrogen embrittlement, stress corrosion delayed cracking and fatigue fracture, after laser heat treatment, the highest hardness of the welding seam can be generally reduced by more than 50HV, the toughness of the welding seam is improved, and the risks of hydrogen embrittlement, stress corrosion delayed cracking and fatigue fracture of the welding seam are reduced.

The weld joint after the laser heat treatment has at least a tempered martensite structure after the laser heat treatment, and the tempered martensite structure, a martensite structure (or none), a ferrite and martensite dual-phase structure, and a tempered martensite structure can be formed in this order from the surface to the inside. When the member is thick, the original martensite structure remains.

Adopting multiple laser heat treatment, firstly adopting a laser processing device to carry out the first laser heat treatment on the welding seam to obtain higher surface temperature (such as more than or equal to 900 ℃); then at least one laser heat treatment is carried out on the welding seam by adopting a laser treatment device, and the surface temperature is lower than Ac3 (less than or equal to 900 ℃).

As shown in fig. 3, Q0 is a curve of the weld temperature T without laser heat treatment as a function of time T, Q1 is a curve of the weld temperature T with laser heat treatment for the first time as a function of time T, and Q2 is a curve of the weld temperature T with laser heat treatment for the second time as a function of time T. After welding, the weld temperature will drop rapidly with time, and the molten structure then transforms into a large amount of martensite, even widmannstatten. After welding, the laser heat treatment is timely applied to the welding seam of the component to heat the surface of the welding seam, and the welding residual heat of the welding seam is utilized to prolong the tissue transformation time. In order to obtain good laser heat treatment effect, the timing of the laser heat treatment of the welding seam is within a period of time after welding, and the timing of the laser heat treatment is generally controlled within 30 seconds after welding. After the welding is completed for more than 30 seconds, the weld temperature may decrease to room temperature. The formation of martensite can be reduced by prolonging the cooling speed, the proportion of tempered martensite is improved, even a martensite and ferrite dual-phase structure can be obtained, the structure has extremely excellent plasticity, and the risks of delayed cracking and fatigue fracture of a welding seam can be effectively reduced. In addition, under the influence of the residual heat of the welding seam, the effect of tempering the martensite in the welding seam can be effectively realized by carrying out the laser heat treatment again, the shorter the interval time between the laser heat treatment again and the laser heat treatment for the first time is, the better the interval time between the laser heat treatment again and the laser heat treatment for the first time is, and the interval time between the heating in stages and in steps can influence the martensite tempering effect. And the dimension control precision of the laser heat treatment range is higher, and the temperature control is precise.

As shown in fig. 4, a laser processing apparatus A3 is disposed after the welding of the components, and if the welding is performed by a laser tailor welding method, and the welding apparatus a2 is a laser welding apparatus, the laser processing apparatus A3 may use the same laser source as the welding apparatus a2, and of course, the welding apparatus a2 and the laser processing apparatus A3 may use laser sources separately. Wherein AA' is the welding direction.

The laser heat treatment device A3 can be independently arranged on another set of machine tool for increasing the laser heat treatment time if the welding mode is resistance spot welding, the laser heat treatment device A3 is adopted after the resistance spot welding, the laser heat treatment is implemented through the operation of a mechanical arm, the laser heat treatment can realize manual control, and is synchronous or asynchronous with the welding device A2, and the laser heat treatment in the forms of laser annealing or tempering and the like is carried out after the welding is finished, but the mode can increase the welding seam treatment time and reduce the production efficiency. The asynchronous control has the advantage of realizing longer heating and heat preservation or realizing secondary and repeated circulating laser heat treatment.

To achieve high production efficiency, the shielding gas device a1, the welding device a2, the laser processing device A3, and the non-contact temperature measuring device a4 (if included) may be mounted on the same machine tool movement unit, moving with the welding device a 2.

As shown in fig. 5, the laser processing apparatus a3 may specifically include: laser transmission optic fibre D1, fiber splice D2, fiber connection module D3, collimation module D4, laser beam shaping module D5, focusing mirror module D6 and protection mirror module D7. In some embodiments, for example, a total reflection laser module can be further added to change the transmission direction of the laser.

If a non-contact temperature measuring device A4 is adopted, such as a temperature measuring instrument with the modes of infrared induction temperature measurement, laser reflection temperature measurement and the like, a plurality of temperature measuring instruments can be installed to realize continuous detection of the temperature of the welding seam, the temperature of the surface of the welding seam of laser heat treatment in the forms of laser annealing or tempering and the like is measured by adopting the non-contact temperature measuring device A4, and after the temperature data and the laser heat treatment process data in the forms of laser annealing or tempering and the like are processed by a computer (not shown in the figure), the feedback control of the laser power of the laser processing device A3 can be realized. For steel grades with low annealing or tempering requirements, parameters such as welding speed, laser power, scanning range and the like can be directly adjusted according to the quality requirement of a welding seam, the measurement control process is simplified, and a non-contact temperature measuring device A4 is omitted.

As shown in fig. 6, after the laser spot E1 focused by the laser is processed by the laser shaping module D5, the laser spot E1 can be scanned on the X-axis and Y-axis according to a certain motion requirement E2, such as a circle, a sine, a spiral, etc. The laser is swept within a desired range E3, such as an elliptical range, a rectangular range, referred to as a spot. The annealing or tempering laser scanning spot size generally satisfies: the scanning length along the welding direction AA' (X axis) is more than or equal to 5 mm. The scanning width is 2mm or more in the direction perpendicular to the welding direction AA' (Y axis). The length of the scan along the welding direction (X axis) is adjusted according to the welding speed, and the width of the scan along the direction perpendicular to the welding seam (Y axis) is adjusted according to the width of the welding seam. The speed of movement of the entire area of the scan is referred to as the heat treatment speed.

The weld joint of the laser tailor-welded carbon steel generally has a martensite structure, particularly high-strength steel such as DP steel, TRIP steel and hot forming steel for automobiles, the weld joint can form a full martensite structure, the toughness of the weld joint structure is too low, and the weld joint is easy to crack during material production or use. In order to improve the toughness of the welding seam, the welding seam can be subjected to heat treatment modes such as annealing and tempering treatment by laser, so that the hardness of the welding seam region is reduced, and the toughness of the welding seam is improved.

Because the laser heats the surface of the welding seam, the heat is transferred to the center or the lower surface of the welding seam through the heat of the metal, and when the temperature of the surface of the welding seam is higher, texture structures with different temperatures such as tempering, annealing, quenching and the like can appear from the center of the welding seam to the surface. The welding seam of the high-strength steel is subjected to one-time laser heat treatment, when the surface temperature is 1400 ℃, the structure of the welding seam from the surface to the lower surface can be obviously seen under a metallographic microscope, and the structure is as follows: the steel plate comprises a surface quenching structure, a transition region and tempered martensite, wherein the transition region can see complex metallographic structures such as ferrite and martensite dual-phase structures. When the thickness of the part is large, a small amount of the structure remains before the laser heat treatment because the lower surface temperature is not high. When the surface quenching structure, namely the welding seam is subjected to heat treatment, after the original welding seam structure is austenitized due to high temperature on the surface, the quenched martensite structure is formed by the welding seam matrix with a cooling effect, the outer side of the surface quenching structure usually has oxide residues, and the thickness of the oxide is reduced or even disappears when the laser heat treatment is carried out under the protective gas atmosphere.

From the material science perspective, after the martensite structure in the welding seam is tempered, the hardness of the martensite structure can be reduced, and the effect of softening the welding seam can be achieved. For example, the target tempering temperature range for the weld martensite structure is 300 ℃ to 730 ℃, and for example, the high temperature tempering temperature is 500 ℃ to 730 ℃, when the laser heat treatment speed is slower, or the part is thinner, the surface temperature of the part can be slightly higher than the target tempering temperature, for example, for a part with a thickness of 0.8mm, the laser heat treatment speed is 0.5 meter per minute, and the surface temperature can be 600 ℃ to 1000 ℃. When the laser heat treatment is faster or the part is thicker, the surface temperature of the part should be further increased to ensure that most of the martensite structure is tempered, e.g. for a part 3.0mm thick, the laser heat treatment is 4 meters per minute and the surface temperature of the part may be 1000 ℃ to 1500 ℃. If slow laser heat treatment is adopted, laser tempering can be carried out at a lower temperature, such as 400-730 ℃, so as to prolong the heating time, thereby avoiding the formation of a quenching structure on the surface and simultaneously obtaining good welding seam toughness. With the rapid laser heat treatment, in order to obtain good weld toughness, a quenched structure, i.e., a martensite structure, or a martensite and ferrite dual-phase structure is inevitably formed on the surface. In this case, in order to reduce the hardness of the surface-quenched structure, a second laser heat treatment may be performed to perform a tempering treatment, and the tempering treatment may be performed again at a temperature of 300 to 730 ℃ or higher. If the material is thicker or the requirement on the uniformity of the finally formed welding seam martensite tempered structure is higher, multiple times of laser heat treatment can be carried out to realize multiple times of tempering treatment, and the temperature range of the laser heat treatment can be reasonably distributed according to the process requirement, so that the uniformity of the welding seam martensite tempered structure is improved.

For the tempering type laser heat treatment, the martensite structure in the weld joint is tempered and then the tempered martensite structure is obtained in the tempering temperature region. Taking laser irradiation at 1400 ℃ on the surface of a weld as an example, when the tempering temperature is low, for example, in the area of a part with the thickness of 2.0mm close to 400 ℃ of the lower surface, carbide precipitation can be seen on the tempered martensite structure. At higher tempering temperatures, e.g., in the region of the 2.0mm thick part near the upper surface at about 650 ℃, the martensite structure is seen to decompose. The ferrite and martensite dual-phase regions exist near the laser irradiation surface, and under the influence of the cooling rate, a martensite structure which is not self-tempered fully can exist outside the dual-phase regions, and a martensite structure which is self-tempered can exist outside the structure. When the cooling rate is sufficient, no self-tempered martensite structure is apparent at the outermost side. Generally, the rapid laser heat treatment is suitable for efficient production rhythm, the thickness proportion outside a double-phase region is small, and the influence on the overall toughness of a welding seam is small.

If the laser heat treatment is carried out on the weld joint by taking annealing as a target, more martensite and ferrite dual-phase structures or ferrite and pearlite structure annealing structures can be formed, the toughness of the weld joint after annealing can be improved more obviously, the weld joint after austenitizing can be rapidly cooled due to the influence of a cold-state base material, and the dual-phase steel structure is common. The purpose of annealing the weld is to extend the laser annealing time and heat the weld to obtain enough partial or full austenite to obtain more annealed microstructure. The annealing temperature range of the welding seam is 740-850 ℃. The surface temperature of the part may be heated to slightly above this target temperature, for example, for a 0.8mm thick part, the laser heat treatment speed may be 0.5 meters per minute and the surface temperature may be 800 ℃ to 950 ℃. For example, for a 2.0mm thick part, the heat treatment rate is 0.1 meters per minute and the surface temperature may be 800 deg.C to 1200 deg.C. When the velocity is sufficiently low, the surface temperature may be set to the critical zone quench temperature, e.g., 740 ℃ to 850 ℃. The speed is reduced, mainly for the purpose of more uniform annealing structure of the welding seam.

In order to achieve a rapid heat treatment of the far end of the laser heat treated surface, for example, to shorten the time between welding and laser heat treatment, when the part thickness is large, the laser irradiated surface may reach a melting point or even a boiling point, for example, a surface temperature of 1500 ℃, at the center of the part where the double-sided laser heat treatment is performed or at another surface position of the single-sided laser heat treatment head. Therefore, in order to improve the toughness of the weld joint, the surface temperature of the part does not have a certain fixed temperature, the overall toughness of the weld joint is comprehensively considered, and the weld joint can be comprehensively evaluated by adopting a repeated bending fatigue test, a cupping test, a tensile test, a hardness test and the like. And the quenching hardening area of the laser irradiation surface can realize the performance of the whole welding seam to be consistent through multiple times of tempering or annealing.

After the tempering treatment is carried out by the laser heat treatment, for the weld zone where the surface quenching occurs, the hardness may appear to be first higher, then suddenly lower, and then gradually higher from the laser irradiation surface to the far end. This phenomenon is related to the distribution of the martensite structure, the two-phase region, the high-temperature tempered martensite structure, and the low-temperature tempered martensite structure. After multiple tempering treatments, the hardness close to the laser irradiation surface is reduced, the hardness is also reduced under the influence of heat transfer in the interior of the structure, a two-phase region is pushed inwards possibly, and the tempering range and the tempering degree of a martensite structure are enlarged.

After laser heat treatment, when the highest hardness of the welding seam is reduced by more than 10HV after laser annealing treatment, the heat treatment effect begins to appear; when reduced above 50HV, weld toughness improvement begins to manifest; when the weld toughness is reduced to more than 100HV, the weld toughness is improved obviously.

The laser heat treatment is to heat the surface of the weld, the surface atomic heat is transferred to the far end of the laser irradiation, such as the center and the lower surface of the weld, if the heat treatment speed is high and the length of the X axis of the scanning light spot is short, the surface is improved in microstructure, the inside is not fully improved, even the surface quenching phenomenon occurs due to the overhigh surface temperature, in order to avoid the surface laser quenching during the laser heat treatment of the weld, the suitable method is to increase the scanning length of the X axis and reduce the heat treatment speed.

In order to further improve the annealing or tempering treatment effect realized by the laser heat treatment and obtain a uniform structure from the center of the welding seam to the surface, a plurality of laser treatment devices A3 can be arranged to realize segmented laser heat treatment and slow cooling, thereby avoiding the laser surface quenching phenomenon or improving the tempering efficiency of the welding seam. Laser processing devices A3 may be mounted on the upper and lower surfaces of the weld seam, respectively, to reduce the temperature difference between the upper and lower surfaces.

The laser heat treatment aims to improve the toughness of a welding seam, and steel types which are easy to fracture the welding seam often have a large amount of martensite structures or even all martensite structures in the welding seam, the highest hardness of the steel types in the welding seam is more than or equal to 250HV and even can reach more than 700HV under the common condition. Therefore, the invention is mainly suitable for high-strength steel with the tensile strength of more than or equal to 900MPa after water-cooling quenching, and the highest hardness of the weld zone of the steel without laser annealing or tempering is generally more than or equal to 300 HV. For the ultrahigh-strength steel with the tensile strength of more than or equal to 1500MPa after water-cooling quenching, the highest hardness of a welding seam area without laser annealing or tempering is generally more than or equal to 500HV, and the risks of delayed cracking and fatigue fracture are further improved. When annealing production is needed, the ultra-high strength steel before welding is in a cold rolling state and a hot rolling state, the microstructure mainly comprises ferrite and pearlite, and a large amount of martensite structures exist in a welding line after laser welding. Finished materials, such as DP steel, martensitic steel, hot formed steel, etc., also have a significant amount of martensite structure in the weld area. After spot welding of the parts, the spot welding position of the steel is a microstructure mainly comprising a martensite structure. The laser is adopted to quickly scan the welding position, so that the tempering purpose can be achieved.

More importantly, the laser heat treatment can reduce the risk of delayed cracking of the weld. The steel with the tensile strength of more than or equal to 1200MPa has the risk of delayed cracking, and the risk of stress corrosion cracking is also increased. Laser heat treatment gives some more suitable solutions.

The first scheme is as follows: firstly, adopting laser heat treatment to obtain higher surface temperature (such as more than or equal to 900 ℃), and tempering partial martensite structure below the surface of a welding line through heat transfer; then, laser heat treatment is carried out again, the surface temperature is lower than Ac3 (less than or equal to 900 ℃), and the surface of the welding seam is annealed or tempered. In the secondary laser heat treatment, the surface of the weld is tempered in a two-phase region of austenite and ferrite, whereby a martensite-ferrite two-phase structure is obtained in a large amount, and when the surface is tempered at a temperature lower than Ac3, the surface is a tempered martensite structure.

The second scheme is as follows: the laser heat treatment is adopted for the first time, the surface temperature is lower than Ac3 (less than or equal to 900 ℃), and the surface of the welding seam is annealed or tempered. Naturally, because of the low surface temperature of this solution, the central martensitic structure is tempered to a lower degree than the first for thicker parts. However, if the microstructure of the surface is improved significantly, the crack sensitivity is greatly reduced if a two-phase structure is obtained. The stress corrosion of the surface and the delayed cracking risk of hydrogen embrittlement can be effectively controlled.

Therefore, for the material with poor overall toughness of the welding seam, the first scheme of realizing part core tempering, surface annealing and tempering by adopting multiple laser heat treatments is more suitable. In addition, if the weld is still not improved in the first embodiment, it is considered that laser heat treatment is performed on the upper and lower surfaces of the weld of the component at the same time. However, due to the influence of the structure of the components and the arrangement of the equipment, the double-side laser heat treatment may have certain operation difficulty. The parts include steel in the form of automobile parts, hot rolled strip, slabs, cold rolled strip, and the like.

In the processes of laser tailor welding, electric arc welding and the like, the laser is adopted to preheat the edge part of the welding seam material, and heat and preserve heat at two sides during welding to form large-range heating at two sides of a welding position, even before and after welding, thereby further solving the tempering problem of the martensite structure of the welding seam. The control of the structure transformation path is realized by controlling the cooling path of the welding area through laser heat treatment. For example, the structure control of the dual-phase steel, after the welding seam is cooled to the temperature of the austenite and the ferrite critical region, the laser heat treatment is adopted to supplement heat to the welding seam, and enough ferrite transformation time is kept, so that a part of ferrite structure is obtained, and the occurrence of full martensite structure is prevented.

The chemical components and the mass percentage of the high-strength steel generally meet the following requirements: c%: 0.08-0.70%, Mn%: 0.5% -3.0%, B%: 0.0008 to 0.008 percent. Other elements for strengthening or grain refining, such as Ni, Cr, Mo, V, Ti, Nb and the like are added, and the elements can be added singly or compositely. If these alloying elements are added, at least one of the following two conditions should be satisfied: the total content of Ni, Cr and Mo is more than or equal to 0.05 percent; the sum of the contents of V, Ti and Nb is more than or equal to 0.01 percent.

The two materials of the laser tailor-welding can be the same material or two different materials. But the chemical components and the mass percentage of at least one of the two materials of the laser tailor-welding meet the following requirements: c%: 0.18% -0.60%, Mn%: 0.3% -3.0%, B%: 0.0008 to 0.008 percent. Other elements for strengthening or grain refining, such as Ni, Cr, Mo, V, Ti, Nb and the like are added, and the elements can be added singly or compositely. The alloying elements should satisfy the condition that the sum of the contents of Ni, Cr and Mo is more than or equal to 0.05 percent, or satisfy the condition that the sum of the contents of V, Ti and Nb is more than or equal to 0.01 percent.

Preferably, the method comprises the following steps: the chemical components and the mass percentage of one of the materials for tailor-welding meet the following requirements: c%: 0.27% -0.47%, Mn%: 0.3% -2.5%, B%: 0.0008 to 0.005 percent. Other elements for strengthening or grain refining, such as Ni, Cr, Mo, V, Ti, Nb and the like are added, and the elements can be added singly or compositely. The alloying elements should satisfy the condition that the sum of the contents of Ni, Cr and Mo is more than or equal to 0.05 percent, or satisfy the condition that the sum of the contents of V, Ti and Nb is more than or equal to 0.01 percent.

Further preferably: the chemical components and the mass percentage of one of the materials for tailor-welding meet the following requirements: c%: 0.32% -0.37%, Mn%: 0.3% -0.8%, B%: 0.001 to 0.005 percent. Other elements for strengthening or grain refining, such as Ni, Cr, Mo, V, Ti, Nb and the like are added, and the elements can be added singly or compositely. The alloying elements should satisfy the condition that the sum of the contents of Ni, Cr and Mo is more than or equal to 0.05 percent, or satisfy the condition that the sum of the contents of V, Ti and Nb is more than or equal to 0.01 percent. Wherein the Cr%: 0.1% -0.5%, Mo%: 0.1% -0.5%, Ni%: 0.1% -0.5%, Ti%: 0.01% -0.06%, Nb%: 0.01 to 0.07 percent.

In order to illustrate the characteristics and effects of the present invention, the following will be described by comparing specific examples and experimental data, but the present invention is not limited to the following description:

as shown in fig. 4, a laser processing apparatus A3 using the same laser light source as the laser welding apparatus a2 was provided after the laser tailor welding. The shielding gas device a1, the laser welding device a2, the laser processing device A3, and the non-contact temperature measuring device a4 are mounted on the same robot arm and move together with the laser welding device a 2.

As shown in fig. 5, the laser processing apparatus a3 includes necessary modules such as a laser transmission fiber D1, a fiber splice D2, a fiber connection module D3, a collimation module D4, a laser shaping module D5, a focusing mirror module D6, and a protection mirror module D7.

As shown in fig. 6, after the laser point E1 is processed by the laser shaping module D5, the laser point E1 is scanned at the weld position approximately in the X-axis and Y-axis according to the sine E2, and an approximate rectangular range E3 is formed. The size of the annealing and tempering laser scanning light spot meets the following requirements: the scan length in the welding direction (X-axis) was 20 mm. The scanning width was 3mm in the direction perpendicular to the welding direction (Y-axis).

The main chemical components and the mass percentage content of the tailor-welded material are shown in table 1.

TABLE 1 Main chemical composition and mass percentage of tailor-welded material

After the laser heat treatment process and the laser heat treatment, the properties of the welding seam subjected to the laser heat treatment, such as hardness, delayed fracture, fatigue and the like, are obviously improved. Particularly, after the process of 1400 ℃ plus 650 ℃ is adopted for multiple times of laser heat treatment, the hardness of the welding line is obviously reduced. In practical application, the proper laser heat treatment temperature is selected according to the service requirements of the base material, so that the welding seam is prevented from being too hard or too soft.

And (4) corroding the tested welding seam sample by 4% nitric acid alcohol, and observing the obtained metallographic structure. As shown in FIG. 7, a typical metallographic structure of a weld which had been subjected to laser heat treatment at 1400 ℃.

Fig. 8 shows a typical layered structure diagram of a 1400 ℃ +650 ℃ laser heat-treated weld bead, which sequentially comprises a tempered martensite structure L1, a martensite structure L3 (the layer may not exist), a ferrite and martensite dual-phase structure L5 (or tempered martensite structure), and a tempered martensite structure L7 from the surface to the inside. When the member is thick, the original martensite structure remains.

In conclusion, the technical scheme of the laser treatment method and the system for the weld joint of the high-strength steel has the advantages that the adopted laser heat treatment temperature precision is high, the heat treatment range size is precise, the laser heat treatment can well solve the problem when the electromagnetic induction heat treatment cannot be implemented under the working conditions of limited space and complex parts, and the weld joint of the parts is subjected to heat treatment on a three-dimensional structure through mechanical structures such as a mechanical arm. Particularly, the laser heat treatment can realize the heat treatment of a surface two-phase region, and can relieve the risks of hydrogen embrittlement, stress corrosion delayed cracking and fatigue fracture of the welding seam when enough high strength is kept in the welding seam. Due to the penetration of the magnetic induction lines, the electromagnetic induction heat treatment is not easy to realize the layered control of the microstructure. Compared with laser surface quenching, tempering and annealing technologies aiming at parts such as gears, semiconductors and the like, the invention breaks through the application range of laser heat treatment, creatively utilizes the welding residual temperature and the peripheral preheating of welding seams, prolongs the cooling time, reduces the cooling speed, obtains a large amount of tempered martensite structures, even ferrite and martensite dual-phase structures, and adopts multiple laser heat treatment aiming at the welding seams to obtain the internal tempered martensite and the ferrite and martensite dual-phase structures on the surfaces or close to the surfaces, thereby greatly improving the toughness of the welding seams and avoiding the risks of hydrogen embrittlement, stress corrosion delayed cracking and fatigue fracture of the welding seams.

It should be noted here that, in other embodiments, the following alternatives may also exist:

1. the surface of the welding seam is heated at high temperature once by laser to form a surface quenching structure, namely surface hardening. Due to the heat transfer effect, the martensite tempering inside the welding seam is realized, but the laser surface quenching structure still exists on the surface of the welding seam, so that the quality of the welding seam can be improved to a certain extent.

2. The laser tempering is adopted to temper the surface of the welding seam, so that the martensite hardness of the surface of the welding seam can be reduced to a certain extent, and the quality of the welding seam is improved.

3. Performing laser heat treatment in steps, such as heating to the martensite tempering temperature for the first time, and preserving heat for a period of time; heating to austenite and ferrite dual-phase region for the second time, and keeping the temperature for a period of time. And the phase change temperature and time are controlled to obtain stable phase composition ratio.

4. In the welding line cooling process, the welding line is cooled to a certain specific temperature interval, the laser heat treatment is adopted for heat supplement, the phase change time is controlled, and the required phase proportion and phase composition are obtained. And performing temperature control on the welding seam by adopting various auxiliary modes such as laser, electromagnetic induction, heat insulation materials and the like to obtain the required welding seam microstructure.

5. The tissue structure of the welding seam adopts multiple laser heat treatment or controls the temperature of the laser heat treatment, and the welding seam can only have certain layers of tissues, such as:

(1) the welding seam after laser heat treatment sequentially comprises the following parts from the surface to the inside: tempered martensite structure, ferrite and martensite dual-phase structure (or tempered martensite structure), tempered martensite. When the member is thick, the original martensite structure remains.

(2) The welding seam after laser heat treatment sequentially comprises the following parts from the surface to the inside: a ferrite and martensite dual-phase structure (or tempered martensite structure), and a tempered martensite structure. When the member is thick, the original martensite structure remains.

(3) The welding seam after laser heat treatment sequentially comprises the following parts from the surface to the inside: martensite structure, ferrite and martensite dual-phase structure (or tempered martensite structure), tempered martensite. When the member is thick, the original martensite structure remains.

(4) The welding seam after laser heat treatment sequentially comprises the following parts from the surface to the inside: a tempered martensite structure. When the member is thick, the original martensite structure remains.

The above description is only a preferred embodiment of the present invention, and is not intended to limit the scope of the present invention, and all modifications and equivalents of the present invention, which are made by the contents of the present specification and the accompanying drawings, or directly/indirectly applied to other related technical fields, are included in the scope of the present invention.