CN115679316A

CN115679316A - Method for laser implantation material increase of cutting tooth

Info

Publication number: CN115679316A
Application number: CN202211458160.1A
Authority: CN
Inventors: 请求不公布姓名
Original assignee: Hengpu Ningbo Laser Technology Co ltd
Current assignee: Hengpu Ningbo Laser Technology Co ltd
Priority date: 2022-11-21
Filing date: 2022-11-21
Publication date: 2023-02-03

Abstract

The application relates to the technical field of laser implantation and discloses a method for laser implantation material increase of a cutting pick. According to the method, the laser implantation process parameters are optimally selected, so that the phenomenon that a wear-resistant layer formed by the ceramic material with the high volume fraction is easy to crack is improved from the process angle by controlling the interface reaction condition on the premise that the ceramic material has the high volume fraction, and a foundation is laid for using the ceramic material in a large proportion by using the composite material.

Description

Method for laser implantation additive of cutting tooth

Technical Field

The application relates to the technical field of laser implantation, in particular to a method for laser implantation material increase of cutting teeth.

Background

In the fields of steel, metallurgy, molds and the like, abrasion is one of the main causes of material loss and energy waste. With the rapid development of modern industry, under many severe working conditions, a simple steel metal material cannot meet the use requirements. The ceramic particle reinforced metal matrix composite material has the advantages of high strength, high hardness, high wear resistance and the like, and is one of effective ways for solving the problem of material failure under complex and severe working conditions.

At present, the main processes for preparing the wear-resistant material layer on the metal substrate comprise surfacing, ion injection, spraying, laser cladding and the like, and compared with the traditional surfacing, spraying and other processes, the laser cladding technology has the characteristics of high energy, low dilution rate and small heat affected zone and is widely accepted. As a laser implantation (laser melt implantation) technique which is the same as the laser cladding technique, the metal matrix is melted and the ceramic particles are not substantially melted, the ceramic particles are not directly irradiated by laser, the ceramic reinforced particles enter a molten pool in a solid state, and under the condition that liquid metal is rapidly cooled, the particles are "frozen" in the molten pool to form a particle reinforced wear-resistant composite material layer, and a schematic diagram is shown in fig. 1. The laser implantation technology has unique advantages in the aspects of controlling cracking and particle melting, and is an ideal method for preparing the particle reinforced wear-resistant composite material layer.

The ceramic reinforcing phase has excellent performances such as high hardness, high strength, high elastic modulus and the like, common ceramics comprise carbide ceramics, oxide ceramics, nitride ceramics, composite ceramics and the like, wherein tungsten carbide ceramics have good comprehensive performances in all aspects, so the tungsten carbide ceramics are widely applied in the industrial field as the reinforcing phase. Although the hardness and the wear resistance of the composite material can be improved along with the increasing proportion of the ceramic material, the wear-resistant layer cracks due to the accumulation of thermal stress caused by the difference of the thermal expansion coefficients.

Ye et al prepared V with different volume fractions by cast infiltration ₈ C ₇ The hardness of the reinforced Fe-based composite material tends to increase along with the increase of the volume fraction of the reinforced phase, and the impact toughness is increased by 8.1J/cm ² Reduced to 4.7J/cm ² When the volume fraction of reinforcing phase is less than 24%, the abrasion resistance is dependent on V ₈ C ₇ The content is increased to be enhanced, and when the volume fraction exceeds 24%, the breakage of particles and the generation of microcracks lead to a decrease in wear resistance. The composite electro-metallurgical casting process of Zhang Ning and other technological steps to prepare WC/5CrNiMo composite material has increased hardness and wear resistance, and lowered toughness resulting in far lower wear resistance than that of two-body friction wear.

From the research results, the ceramic particle reinforced metal matrix composite material can obviously improve the matrix hardness and improve the wear resistance to a certain extent. However, as the proportion of ceramic particles increases, the wear resistant layer formed from the composite material is susceptible to cracking. According to the research content in the early stage, the ceramic composite material is applied to the laser implantation technology, so that the cutting tooth is subjected to material increase through the laser implantation process, the wear resistance of the cutting tooth is improved, and the cracking situation is improved.

Disclosure of Invention

In view of the above, an object of the present invention is to provide a method for laser-implanting additive into a cutting pick, so that the cracking of a wear-resistant layer on the surface of the cutting pick is improved and the cutting pick has high hardness on the premise of high volume fraction of a ceramic material in a ceramic composite material.

To solve the above technical problems/achieve the above object or to at least partially solve the above technical problems/achieve the above object, the present application provides a method of laser implanting additive for a cutting pick, including:

step 1, preprocessing a cutting tooth additive surface; drying the ceramic composite material, wherein the volume fraction of the ceramic material in the ceramic composite material is more than or equal to 50 percent;

step 2, preparing a surface wear-resistant strengthening layer from the pretreated cutting pick and the ceramic composite material through a laser implantation process; wherein the laser implantation parameters are:

the laser power density is 200-400W/mm ² The laser scanning speed is 0.4-1.5m/min, the spot diameter is 2-5mm, the included angle between the powder feeding head and the cutting tooth additive surface is 35-55 degrees, and the powder feeding head and the cutting tooth additive surface form an angle of 35-55 degreesThe linear distance of the surface is 4-8mm.

Optionally, the pretreatment is to polish the additive surface of the cutting tooth to be clean so that the base material is completely exposed; cleaning the polished area with alcohol or acetone to make it completely clean; the ceramic composite material is dried after being cleaned by alcohol, and the drying temperature is 120-200 ℃.

Optionally, the laser power density is 290-400W/mm ² (ii) a In certain embodiments of the present application, the laser power density may be specifically selected from 200W/mm ² 、290W/mm ² 、320W/mm ² 、350W/mm ² Or 400W/mm ² 。

Optionally, the laser scanning speed is 1.3-1.5m/min; in certain embodiments of the present application, the laser scanning speed can be specifically selected from 0.4m/min, 0.6m/min, 0.8m/min, 1.0m/min, 1.3m/min, or 1.5m/min.

Optionally, the diameter of the light spot is 3-4mm; in some embodiments of the present application, the spot diameter may be specifically selected from 2mm, 3mm, 4mm, or 5mm.

Optionally, the included angle between the powder feeding head and the additive surface of the cutting pick is 40-50 degrees; in some embodiments of the present application, the powder feed head and the cutting pick additive surface are at an angle of 35 °, 40 °, 45 °, 50 °, or 55 °.

Optionally, the linear distance from the powder feeding head to the cutting pick additive melting pool is 4mm, 5mm, 6mm, 7mm or 8mm.

Optionally, the laser implantation parameters in the method of the present application further include a powder feeding amount of 1.5-3.6g/min; in certain embodiments of the present application, the powder delivery is 1.5g/min, 2.0g/min, 2.4g/min, 3.0g/min, or 3.6g/min.

Optionally, the ceramic composite material comprises or consists of a ceramic material and a metallic material; wherein the ceramic material is selected from one or more than two of carbide, nitride, oxide and boride; in certain embodiments of the present application, the ceramic material is selected from carbides or oxides.

In certain embodiments of the present application, the ceramic composite has a particle size of (40-150) μm ± 5 μm; alternatively, the particle size is 40 μm, 50 μm, 60 μm, 70 μm, 80 μm, 90 μm, 100 μm, 110 μm, 120 μm, 130 μm, 140 μm, or 150 μm.

The metal material in the ceramic composite material is an aluminum-based metal material, an iron-based metal material, a nickel-based metal material or a titanium-based metal material;

wherein, optionally, the aluminum-based metal material is pure aluminum and/or aluminum alloy; in certain embodiments of the present application, the aluminum alloy is an AlSi10Mg aluminum alloy; in other embodiments of the present application, the AlSi10Mg aluminum alloy has a chemical composition as shown in table 1:

TABLE 1AlSi10Mg aluminum alloy chemical composition (wt%)

Fe

Mg

Mn

Cu

Si

Al

AlSi10Mg

0.14-0.55

0.40-0.45

≤0.01

≤0.05

10-11

Bal. (balance)

Optionally, the iron-based metal material is pure iron and/or an iron alloy; in certain embodiments herein, the ferrous alloy is 0Cr18Ni9 ferrous alloy (abbreviated 304) or Q235 steel; in other embodiments of the present application, the 0Cr18Ni9 iron alloy has a chemical composition as shown in table 2:

TABLE 2 0Cr18Ni9 ferroalloy chemical composition (wt%)

C

Cr

Ni

Mn

Si

Fe

0Cr18Ni9

＜0.08

＜18.5

＜9.4

＜1.82

＜0.91

Bal. (balance)

The Q235 steel has the chemical composition shown in Table 3:

TABLE 3Q235 Steel chemistry (wt%)

C

S

P

Si

Mn

Fe

Q235 steel

0.17-0.22

≤0.0045

≤0.35

≤0.14

Bal. (remainder)

Optionally, the titanium-based metallic material comprises pure titanium and/or a titanium alloy; in certain embodiments of the present application, the titanium alloy is a Ti-6Al-4V titanium alloy (abbreviated as TC 4); in other embodiments of the present application, the Ti-6Al-4V titanium alloy has a chemical composition as shown in Table 4:

TABLE 4Ti-6Al-4V titanium alloy chemical composition (wt%)

Al

Fe

V

C

N

H

O

Ti

Ti-6Al-4V

5.5-6.8

＜0.30

3.5-4.5

＜0.30

＜0.05

＜0.015

＜0.20

Bal. (balance)

Optionally, the nickel-based metallic material comprises pure nickel and/or a nickel alloy; in certain embodiments herein, the nickel alloy is Ni20Cr; in other embodiments of the present application, the Ni20Cr nickel alloy has a chemical composition as shown in table 5:

TABLE 5Ni20Cr Nickel alloy chemical composition (wt%)

	Cr	Ni
			Ni20Cr	20	Bal. (balance)

Optionally, the volume fraction of the ceramic material in the ceramic composite material is more than or equal to 60%; further optionally, the volume fraction of the ceramic material is 60-94%; in certain embodiments of the present application, the volume fraction of the ceramic material may be specifically selected from 50%, 60%, 65%, 70%, 78%, 82%, 89%, or 94%.

Optionally, the ceramic material is selected from one or more of carbides, nitrides, oxides and borides of transition metals in the third to second subgroup of the periodic table, and metals in the fourth to seventh period range, including scandium (Sc), titanium (Ti), vanadium (V), chromium (Cr), manganese (Mn), iron (Fe), cobalt (Co), nickel (Ni), copper (Cu), zinc (Zn), yttrium (Y), zirconium (Zr), niobium (Nb), molybdenum (Mo), technetium (Tc), ruthenium (Ru), rhodium (Rh), palladium (Pd), silver (Ag), cadmium (Cd), lanthanides (La-Lu), hafnium (Hf), tantalum (Ta), tungsten (W), rhenium (Re), osmium (Os), iridium (Ir), platinum (Pt), gold (Au), mercury (Hg), actinides (Ac-Lr), (Rf), (Db), (Sg), (Bh), (Hs), (t), (Ds), (and (mr).

In certain embodiments herein, the transition metal is selected from transition metals from the fourth to sixth periods of the periodic table of elements; in still other embodiments of the present application, the transition metal is a transition metal of the fourth to sixth subgroups of the fourth to sixth periods of the periodic table of the elements; in still other embodiments of the present application, the transition metal is a transition metal of the fourth subgroup or the fifth subgroup of the fourth to sixth periods of the periodic table of elements or tungsten; in still other embodiments of the present application, the transition metal is a transition metal of the fourth subgroup or the fifth subgroup of the fourth period to the fifth period of the periodic table of the elements or tungsten.

Using the same alloy containing WC and ZrO ₂ Metallographic analysis shows that after the ceramic composite material is implanted into a material for material increase by laser, compared with the situation that other process parameters obviously crack, the wear-resistant layer formed by the method avoids cracking; meanwhile, the Vickers hardness is also higher.

According to the technical scheme, the laser implantation process parameters are optimally selected, so that the phenomenon that a wear-resistant layer formed by the ceramic material with high volume fraction is easy to crack is improved from the process angle by controlling the interface reaction condition on the premise that the ceramic material has not high volume fraction, and a foundation is laid for using the ceramic material in a large proportion of the composite material.

Drawings

FIG. 1 is a schematic diagram of a laser implantation process;

FIG. 2 shows SEM and metallographic results for experimental group 1; wherein, the upper figure is a metallographic phase, and the lower figure is an SEM;

FIG. 3 shows SEM and metallographic results for control 1; wherein, the upper figure is a metallographic phase, and the lower figure is an SEM;

FIG. 4 shows SEM and metallographic results for experimental 2 and control 2; wherein a is an experimental group metallographic phase, and b is a control group metallographic phase;

FIG. 5 shows the metallographic results for experimental group 3 and control group 3; wherein a is an experimental group metallographic phase, and b is a control group metallographic phase;

FIG. 6 shows metallographic results for experimental group 4 and control group 4; wherein, a is the metallographic phase of an experimental group, and b is the metallographic phase of a control group;

FIG. 7 shows metallographic results for experimental group 5 and control group 5; wherein a is an experimental group metallographic phase, and b is a control group metallographic phase;

fig. 8 shows metallographic results for experimental 6 and control 6; wherein a is an experimental group metallographic phase, and b is a control group metallographic phase;

fig. 9 is a physical diagram of the cutting pick strengthened by the WC composite material laser implantation and the cutting pick not strengthened under the actual working condition.

Detailed Description

The application discloses a method for laser implantation additive of cutting picks, and a person skilled in the art can appropriately improve the technological parameters by referring to the content. It is expressly intended that all such similar substitutes and modifications apparent to those skilled in the art are deemed to be included in the present application. While the products, processes and applications described herein have been described in terms of preferred embodiments, it will be apparent to those of ordinary skill in the art that variations and modifications in the products, processes and applications described herein, as well as other suitable variations and combinations, may be made to implement and use the techniques of this application without departing from the content, spirit and scope of the application. It should be apparent that the described embodiments are only some of the embodiments of the present application, and not all 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 application.

It should be noted that, in this document, if relational terms such as "first" and "second", "S1" and "S2", "step 1" and "step 2", and "(1)" and "(2)" occur, they are only used for distinguishing one entity or operation from another entity or operation, and do not necessarily require or imply any actual relation or order between these entities or operations. Also, the terms "comprises," "comprising," or any other variation thereof, are intended to cover a non-exclusive inclusion, such that a process, method, article, or apparatus that comprises a list of elements does not include only those elements but may include other elements not expressly listed or inherent to such process, method, article, or apparatus. Without further limitation, an element defined by the phrases "comprising a," "8230," "8230," or "comprising" does not exclude the presence of additional like elements in a process, method, article, or apparatus that comprises the element. Meanwhile, the embodiments and features in the embodiments in the present application may be combined with each other without conflict.

The materials referred to in this application are all commercially available, and in a specific embodiment of this application, the laser cladding apparatus comprises: a German IPG YSL-4000 fiber laser (with the highest power of 4 KW), a KUKA KR-C4 robot control cabinet, a KUKA KR-60HA six-axis linkage mechanical arm, a DPSF-2 double-cylinder powder feeder, an MCW-100 water chiller and a powder feeding device;

in each set of comparative experiments provided in the present application, unless otherwise specified, other experimental conditions, materials, etc. are kept consistent for comparability, except for the differences indicated for each set.

The method for laser implanting additive into cutting picks provided by the application is further explained below.

The first embodiment: the process of the present application

Pretreatment: polishing the surface of the cutting tooth to be implanted with abrasive paper to clean an oxide layer and other stains so as to completely expose the base material; and cleaning the polished area by using alcohol or acetone to completely clean the polished area. And (3) processing the ceramic composite powder, namely cleaning the ceramic composite powder by alcohol, and drying the ceramic composite powder at the temperature of 120-200 ℃ for 2 hours.

Laser implantation: the processed pick and ceramic composite powder can be used for preparing a surface wear-resistant strengthening layer according to a laser implantation process. Wherein, the specific parameters are shown in the following table 6:

TABLE 6

Second embodiment: metallographic analysis of 42CrMo implanted ceramic composite material

In view of the fact that the cutting pick material is generally 42CrMo alloy steel at present, the cutting pick material is taken as a base material in the embodiment, laser implantation material increase is carried out according to the grouping of Table 7, and the crack phenomenon is compared through metallographic analysis, and the result is shown in FIGS. 2-7 and Table 8;

TABLE 7

TABLE 8

Group of	Vickers Hardness (HV) _0.5 )
		Experimental group 1	815
Control group 1	-
		Experimental group 2	741
Control group 2	-
		Experimental group 3	899
Control group 3	-
		Experimental group 4	997
Control group 4	462
		Experimental group 5	850
Control group 5	401
		Experimental group 6	832
Control group 6	-

"-" indicates that the Vickers hardness is measured for a plurality of times due to cracking, and has no practical measurement significance;

the metallographic and SEM results of the experimental group 1 are shown in FIG. 2, a compact continuous reaction layer between WC and an iron matrix completely disappears, and a fine dendritic reactant (Fe-W-C ternary composite carbide) is substituted for the compact continuous reaction layer, so that the accumulation of the thermal stress of a heterogeneous interface is favorably inhibited, the formation of a crack source is effectively avoided, and meanwhile, no crack appears in a metallographic graph; in contrast, the SEM result of the control group 1 shows that the reaction layer of the WC ceramic and the fe matrix is thick, and the reaction layer has a significant crack source, and the metallographic graph shows that the WC ceramic and the fe matrix have significant cracks (fig. 3);

the SEM results of the experimental groups 2 to 6 showed similar phenomena to those of the experimental group 1, the gold phase diagrams (a of fig. 4 to 8) showed no significant cracks, the SEM results of the control groups 2, 3, and 6 showed the same phenomena as those of the control group 1, and the gold phase diagrams (b of fig. 4, 5, and 8) showed significant cracks.

Although no cracking occurred in the control group 4 and the control group 5, it was evident from the gold phase diagrams (b of fig. 6 and 7) of the two groups that the wear-resistant layer had less ceramic particles than the experimental group 4 and the experimental group 5, which resulted in a lower hardness of the wear-resistant layer, probably due to the difference in process parameters that resulted in the suppression of ceramic powder from entering the weld poolThe ceramic content of the wear-resistant layer is far less than a preset value of 70%; meanwhile, according to the results of Vickers hardness shown in Table 8, each experimental group had a higher hardness, while the Vickers hardness of the control group 4 and the control group 5 was only 462HV _0.5 And 401HV _0.5 . The experimental results are combined to see that the proper process conditions can ensure that the wear-resistant layer reaches the preset ceramic content, obtain higher hardness and avoid cracking.

The third embodiment: testing of cutting tooth actual working condition

The laser implantation of the asphalt cutting pick according to the parameters of the experimental group 3 of the second embodiment, using the unreinforced asphalt cutting pick as a comparison, shows that under the condition of asphalt galling with the construction type of 2.5 cm, the asphalt cutting pick strengthened by the laser implantation has the milling square meter number of about 30000 square meters, and the unreinforced asphalt cutting pick has the milling square meter number of about 15000 square meters, so that the actual service life of the cutting pick is improved by 2 times; wherein, fig. 9 is a physical diagram of the appearance of the asphalt cutting pick after the test of the surface strengthening and the non-strengthening, which can clearly show that the non-strengthening cutting pick is more seriously worn than the strengthening cutting pick.

TABLE 9

The above description is merely exemplary of the present application and is presented to enable those skilled in the art to understand and practice the present application. Various modifications to these embodiments will be readily apparent to those skilled in the art, and the generic principles defined herein may be applied to other embodiments without departing from the spirit or scope of the application. Thus, the present application is not intended to be limited to the embodiments shown herein but is to be accorded the widest scope consistent with the principles and novel features disclosed herein.

Claims

1. A method of laser implanting additive cutting picks, comprising:

the laser power density is 200-400W/mm ² The laser scanning speed is 0.4-1.5m/min, the diameter of a light spot is 2-5mm, the included angle between the powder feeding head and the cutting tooth additive surface is 35-55 degrees, and the linear distance from the powder feeding head to the cutting tooth additive melting pool is 4-8mm.

2. The method of claim 1, wherein the laser power density is 290-400W/mm ² 。

3. The method of claim 1, wherein the laser scanning speed is 1.3-1.5m/min.

4. The method of claim 1, wherein the angle between the powder feed head and the cutting pick additive surface is 40 ° to 50 °.

5. The method of any one of claims 1-4, wherein the laser implanting further comprises a powder delivery parameter of 1-5g/min.

6. The method of claim 1, wherein the ceramic composite material comprises a ceramic material and a metallic material, and the ceramic material is selected from one or more of carbides, nitrides, oxides, and borides.

7. The method of claim 6, wherein the metal material is an aluminum-based metal material, an iron-based metal material, a nickel-based metal material, or a titanium-based metal material.

8. The method of claim 1 or 6, wherein the ceramic material is selected from one or more of carbides, nitrides, oxides and borides of transition metals in the periodic table.

9. The method according to claim 8, wherein the transition metal is a transition metal of the fourth to sixth periods of the periodic table.

10. The method according to claim 9, wherein the transition metal is a transition metal of the fourth to sixth subgroups of the fourth to sixth periods of the periodic table.

11. The method according to claim 9, wherein the transition metal is a transition metal of the fourth subgroup or the fifth subgroup of the fourth to sixth periods of the periodic table or tungsten.