CN113430361B - Processing method of high-speed steel wire - Google Patents

Processing method of high-speed steel wire Download PDF

Info

Publication number
CN113430361B
CN113430361B CN202110781924.XA CN202110781924A CN113430361B CN 113430361 B CN113430361 B CN 113430361B CN 202110781924 A CN202110781924 A CN 202110781924A CN 113430361 B CN113430361 B CN 113430361B
Authority
CN
China
Prior art keywords
steel wire
treatment
cooling
speed
temperature
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Active
Application number
CN202110781924.XA
Other languages
Chinese (zh)
Other versions
CN113430361A (en
Inventor
周雪峰
孙驰驰
方峰
涂益友
蒋建清
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Southeast University
Original Assignee
Southeast University
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by Southeast University filed Critical Southeast University
Priority to CN202110781924.XA priority Critical patent/CN113430361B/en
Publication of CN113430361A publication Critical patent/CN113430361A/en
Application granted granted Critical
Publication of CN113430361B publication Critical patent/CN113430361B/en
Active legal-status Critical Current
Anticipated expiration legal-status Critical

Links

Images

Classifications

    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/52—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length
    • C21D9/525—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length for wire, for rods
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • C21D1/19—Hardening; Quenching with or without subsequent tempering by interrupted quenching
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/78—Combined heat-treatments not provided for above
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/78—Combined heat-treatments not provided for above
    • C21D1/785—Thermocycling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/004—Dispersions; Precipitations
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/005—Ferrite

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Heat Treatment Of Strip Materials And Filament Materials (AREA)

Abstract

The invention discloses a processing method of a high-speed steel wire, which comprises the steps of carrying out high-temperature coarsening treatment on the high-speed steel wire, and then carrying out cold processing; and (3) vibrating and refining the steel wire, and then sequentially carrying out alloy clustering treatment, austenitizing treatment and rapid desolventizing treatment to obtain the steel wire. The high-speed steel wire produced by the method has the advantages of small grain size, dispersion distribution of carbide, and good cold processing performance and use performance.

Description

Processing method of high-speed steel wire
Technical Field
The invention relates to a processing method of steel wires, in particular to a processing method of high-speed steel wires.
Background
The high-speed steel has the advantages of high hardness, high wear resistance, good red hardness and the like, is widely applied to manufacturing various efficient and precise processing tools such as milling cutters, gear shaping cutters, turning tools, twist drills, bimetal saw blades and the like, and is an important basic material in the modern high-end equipment manufacturing industry. The high-speed steel tool is made of high-speed steel wires, and the preparation process comprises the following steps: smelting → refining → casting → electroslag remelting → forging → rolling → cold drawing/cold rolling → intermediate annealing → steel wire → product annealing. Due to improper components, structural characteristics and heat treatment process of the high-speed steel, the high-speed steel wire is easy to generate the defects of coarsening of grain size, large carbide particles, small quantity, adhesion and the like in the processing and repeated high-temperature annealing processes, so that the plasticity is lower, the cracking in the cold processing process is caused, the hardness after quenching and tempering is lower, and the processing and use performance of the steel wire are deteriorated.
In order to improve the quality and performance of the steel wire structure of high-speed steel, the prior process method comprises the following steps: the purity of the molten steel is improved through a novel special refining process; s, P and other harmful elements in the steel are reduced; controlling the distribution and size of primary carbides in the steel through microalloying treatment, thermomechanical treatment process optimization and the like; and adopting a complete annealing process or an intermediate annealing process to eliminate dislocation defects and recover the deformability of the steel wire through lattice recombination or atom migration. Although the quality and performance of the structure of the high-speed steel are improved to different degrees by the process method, the produced steel wire still has the problems of larger ferrite grains, less secondary carbides, lower hardness after quenching and tempering, easy cracking during processing and the like.
Disclosure of Invention
The invention aims to: the invention aims to provide a processing method of a high-speed steel wire, which can refine the ferrite grain size of the steel wire, increase the number and the dispersion degree of secondary carbides, and improve the plasticity and the quenching and tempering hardness of the steel wire.
The technical scheme is as follows: the processing method of the high-speed steel wire can improve the structure quality and the performance of the high-speed steel wire. The method comprises the steps of carrying out structure coarsening treatment on a high-speed steel wire, and then carrying out cold machining; and (3) vibrating and refining the steel wire, and then sequentially carrying out alloy clustering treatment, austenitizing treatment and rapid desolventizing treatment to obtain the steel wire.
Wherein the tissue roughening treatment comprises two steps of heat treatment, namely the first step of carbide roughening heat treatment, wherein the heating temperature is 900-1000 ℃, and the heating time is 15 min-1 h; and the second step of carbide graining heat treatment, wherein the heating temperature is 830-860 ℃, and the heating time is 1-2 h.
The steel wire is heated to A by the oscillation thinning treatment1Keeping the temperature above 5-30 ℃ for 15-30 min, and cooling to A1Preserving the heat for 15-30 min at the temperature of 30-60 ℃ below; and circulating for at least five times to oscillate and refine the treatment process.
The clustering temperature of the alloy is 500-600 ℃, and the processing time is 0.5-1 h.
The austenitizing treatment heats the high-speed steel wire to 860-900 ℃ and keeps the temperature for 2-4 h
And (3) cooling the steel wire to 720-760 ℃ at a cooling speed of not less than 2 ℃/min by the rapid desolventizing treatment, preserving the heat for 2-6 h, cooling the steel wire to 500 ℃ in a furnace, and air-cooling the steel wire.
The processing method provided by the invention is used for carrying out structure coarsening treatment on the high-speed steel wire, namely the first step is carbide coarsening heat treatment at the heating temperature of 900-1000 ℃, the second step is carbide graining heat treatment at the heating temperature of 830-860 ℃, and then cold processing is carried out. Subsequently subjecting said wire to an oscillating refining treatment, i.e.At A 1At a temperature of 5-30 ℃ above and A1And circularly heating and cooling in a temperature range of 30-60 ℃ below the temperature, wherein the circulation times are more than 5 times. Clustering the steel wire at 500-600 ℃, heating to 860-900 ℃ for austenitizing, rapidly cooling to 720-760 ℃ at a cooling speed of not less than 2 ℃/min, keeping the temperature for 2-6 h, then cooling to 500 ℃ in a furnace, and discharging. The high-speed steel wire produced by the method has the advantages of small grain size, dispersion distribution of carbide, and good cold processing performance and use performance.
The function of each step of the invention is as follows:
coarsening the structure: a large amount of carbide is dispersed in the high-speed steel structure, so that the cold working plasticity of the high-speed steel is poor. Before the high-speed steel wire is cold-worked, the structure is coarsened to grow the size of carbide, so that the cold-working plasticity of the steel wire is improved. In the first step, carbide coarsening heat treatment is adopted, the temperature is 900-1000 ℃, so that the carbide grows up rapidly, the structure is coarsened, the hardness of the steel wire is reduced, and the deformation capacity is improved. In order to eliminate the bar-shaped carbide which is generated by the carbide coarsening heat treatment and is unfavorable for plasticity, the high-speed steel wire is subjected to carbide graining heat treatment at the temperature of 830-860 ℃, and the aim is to convert the bar-shaped carbide into spherical carbide which is favorable for plasticity and improve the processing plasticity of the steel wire.
Vibrating and refining: although the above treatment is advantageous in cold working plasticity, the steel wire has coarsened ferrite grains and carbides and is disadvantageous in high-speed steel hardness and toughness, and it is necessary to perform a shock refining treatment in A1At a temperature of 5-30 ℃ above and A1And circularly heating and cooling for more than 5 times in a temperature zone at 30-60 ℃. The purpose is as follows: 1) a. the1In the heat treatment process of oscillating up and down at the temperature, the diffusion rate of the alloy elements such as W, Mo, V, Cr and the like is far less than that of the alloy elements
Figure BDA0003155514430000021
The interface migration rate causes alloy elements to be segregated at the interface, so that the interface migration is hindered, and the ferrite grain size is obviously refined; 2) repeated oscillation can greatly increase the unevenness of the alloy elements in the micro-area of the substrate, so that a large amount of alloy elements are generated in the substrateThe segregation zone of the alloying element(s). The segregation of the elements provides a potential nucleation site for subsequent carbide desolventizing treatment, and the size of the carbide is obviously refined.
Alloy clustering treatment: in general, high speed steel wire is directly annealed to relieve working stress without any intermediate treatment, but the structure of the steel wire produced by the above method is relatively coarse. The steel wire is pretreated at 500-600 ℃ before annealing, so that supersaturated solid solution atoms in a matrix are agglomerated to form alloy atom clusters, the desolventizing and precipitation of carbides in the subsequent annealing process are promoted, the spheroidization of the carbides is promoted, the dispersion degree of the carbides is improved, and the structure is refined.
And (3) quick desolventizing: generally, high speed steel annealing uses as low a cooling rate as possible to avoid martensite or bainite transformation, and to reduce the hardness of the steel wire, but tends to cause coarsening of the steel wire structure. The invention leads the high-speed steel wire to be austenitized at 860-900 ℃ and then quickly cooled (not less than 2 ℃/min) to 720-760 ℃ for isothermal temperature. On one hand, after the oscillation treatment and the alloy clustering treatment, a large amount of alloy element agglomeration areas are generated in the matrix, so that the nucleation potential barrier of the carbide is obviously reduced, and a large amount of non-uniform nucleation particles are provided for the desolventizing of the carbide; on the other hand, the higher supercooling degree generated by rapid cooling improves the ferrite nucleation rate, can obviously refine ferrite grains and simultaneously improves the precipitation quantity of carbides. The two aspects act together to improve the dispersion degree of carbide particles and refine the grain size of ferrite, thereby improving the hardness and plasticity of the steel wire after quenching and tempering.
Has the advantages that: compared with the prior art, the invention realizes the effects of refining the structure of the high-speed steel wire and improving the plasticity and the quenching and tempering hardness of the steel wire, so that the grain size of the high-speed steel wire is reduced to be less than 5 mu m from more than 10 mu m, the number density of secondary carbides is improved by more than 20%, the elongation is improved to be more than 17% from about 10%, and the quenching and tempering hardness is improved by 1-2 HRC.
Drawings
FIG. 1 is a photograph of the structure of M42 steel wire obtained by the prior art; the graph (a) is a photograph of grain size, and the graph (b) is a photograph of carbide.
FIG. 2 is a photograph showing the structure of M42 steel wire obtained in example 1; the graph (a) is a photograph of grain size, and the graph (b) is a photograph of carbide.
FIG. 3 is a photograph of the structure of M42 steel wire obtained in example 2; the photograph of the grain size is shown in FIG. a, and the photograph of the carbide is shown in FIG. b.
FIG. 4 is a photograph showing the structure of M42 steel wire obtained in example 3; the photograph of the grain size is shown in FIG. a, and the photograph of the carbide is shown in FIG. b.
FIG. 5 is a grain photograph of M2 steel wire obtained by the prior art; the photograph of the grain size is shown in FIG. a, and the photograph of the carbide is shown in FIG. b.
FIG. 6 is a photograph showing the structure of M2 steel wire obtained in example 4; the photograph of the grain size is shown in FIG. a, and the photograph of the carbide is shown in FIG. b.
FIG. 7 is a photograph showing the structure of M2 steel wire obtained in example 5; the photograph of the grain size is shown in FIG. a, and the photograph of the carbide is shown in FIG. b.
FIG. 8 is a photograph showing the structure of M2 steel wire obtained in example 6; the photograph of the grain size is shown in FIG. a, and the photograph of the carbide is shown in FIG. b.
FIG. 9 shows the quenching and tempering hardness (1200 ℃ quenching +550 ℃ tempering) of the M42 steel wire obtained in examples 1 to 3;
FIG. 10 shows the quenching and tempering hardness (1200 ℃ quenching +550 ℃ tempering) of the M2 steel wire obtained in examples 4 to 6.
Detailed Description
The present invention is described in further detail below with reference to examples.
1) Coarsening the structure: and carrying out two-step heat treatment on the high-speed steel, wherein the first step is carbide coarsening heat treatment at the heating temperature of 900-1000 ℃, and the second step is carbide graining heat treatment at the heating temperature of 830-860 ℃.
2) And carrying out cold machining on the high-speed steel wire subjected to the tissue coarsening treatment according to a conventional production process.
3) Vibrating and refining: heating the steel wire to A1Keeping the temperature above 5-30 ℃ for 15-30 min, and cooling to A1Keeping the temperature below 30-60 ℃ for 15-30 min; and circulating the oscillation refining treatment process for at least five times.
4) Clustering the alloy: heating the steel wire to 500-600 ℃, and preserving heat for 0.5-1 h.
5) Austenitizing: heating the steel wire to 860-900 ℃ and preserving the heat for 2-4 h.
6) And (3) quick desolventizing: and cooling the steel wire to 720-760 ℃ at a cooling speed of not less than 2 ℃/min, preserving the heat for 2-6 h, cooling the steel wire to 500 ℃ in a furnace, and air-cooling.
Example 1:
m42 high speed Steel A1The temperature was about 830 ℃. M42 wire rods with a diameter of 5.5mm were treated as follows:
(1) heating the M42 steel wire to 950 ℃ for 30min, cooling the steel wire to 500 ℃ in a furnace, heating the steel wire to 860 ℃ again for 1h, cooling the steel wire to 500 ℃ in the furnace, and discharging the steel wire from the furnace for air cooling.
(2) The M42 steel wire thus treated was cold drawn.
(3) Heating M42 steel wire to 845 deg.C, maintaining for 20min, rapidly cooling to 780 deg.C, and maintaining for 30 min; the above operation was repeated 5 times in a cycle.
(4) Heating the M42 steel wire to 500 ℃, and preserving the heat for 1 h.
(5) Heating M42 steel wire to 860 deg.C, and keeping the temperature for 4 h;
(6) and (3) rapidly cooling the steel wire to 740 ℃ at a cooling speed of 5 ℃/min, preserving heat for 5 hours, cooling the steel wire to 500 ℃ in a furnace, and taking the steel wire out of the furnace for air cooling.
The structure photograph of the M42 steel wire (phi 4.5mm) after the above treatment is shown in FIG. 2, and it can be seen that the average grain size is 3.4 μ M, and the number density of the secondary carbides reaches 2.0X 106mm-2The total elongation was 17.5%. Figure 9 shows the quenched and tempered hardness of the M42 steel wire to HRC 68.8. In contrast, the grain size of the M42 steel wire with the same specification produced by the conventional process reaches more than 10 μ M, and the number density of the secondary carbides is less than 1.5 multiplied by 106mm-2The total elongation is less than 12%, and the quenching hardness is about 67 HRC. Therefore, the heat treatment method can obviously refine the structure of the high-speed steel wire and improve the plasticity and the quenching and tempering hardness of the steel wire.
Example 2:
m42 wire rods with a diameter of 5.5mm were treated as follows:
(1) heating the M42 steel wire to 1000 ℃ for 15min, cooling the steel wire to 500 ℃ in a furnace, then heating the steel wire to 840 ℃ again for 2h, cooling the steel wire to 500 ℃ in the furnace, and taking the steel wire out of the furnace for air cooling.
(2) The M42 steel wire thus treated was cold drawn.
(3) Heating the M42 steel wire to 850 ℃ and preserving heat for 15min, and then quickly cooling to 770 ℃ and preserving heat for 20 min; the above operation was repeated 5 times in a cycle.
(4) Heating the M42 steel wire to 550 ℃, and keeping the temperature for 1 h.
(5) Heating the M42 steel wire to 870 ℃, and preserving heat for 3 hours;
(6) and (3) rapidly cooling the steel wire to 750 ℃ at a cooling speed of 10 ℃/min, preserving heat for 5 hours, cooling the steel wire to 500 ℃ in a furnace, and discharging and air cooling the steel wire.
The structure photograph and plasticity of the M42 steel wire (phi 4.3mm) after the above treatment are shown in FIG. 3, and it can be seen that the average grain size is 3.8 μ M, and the number density of secondary carbides reaches 2.8X 106mm-2The total elongation was about 19%. Fig. 9 shows the quenched and tempered hardness of the M42 steel wire, HRC 69.0. Therefore, the heat treatment method can obviously refine the structure of the high-speed steel wire and improve the plasticity and the quenching and tempering hardness of the steel wire.
Example 3:
m42 wire rods with a diameter of 5.5mm were treated as follows:
(1) heating the M42 steel wire to 930 ℃ for 1h, then cooling the steel wire to 500 ℃ in a furnace, then heating the steel wire to 850 ℃ again for 2h, cooling the steel wire to 500 ℃ in the furnace, and taking the steel wire out of the furnace for air cooling.
(2) The M42 steel wire processed above was cold drawn.
(3) Heating M42 steel wire to 840 deg.C, maintaining for 30min, rapidly cooling to 780 deg.C, and maintaining for 30 min; the above operation was repeated 5 times in a cycle.
(4) Heating the M42 steel wire to 600 ℃, and keeping the temperature for 1 h.
(5) Heating the M42 steel wire to 890 ℃, and preserving heat for 2 h;
(6) and (3) rapidly cooling the steel wire to 730 ℃ at a cooling speed of 10 ℃/min, preserving heat for 6h, cooling the steel wire to 500 ℃ in a furnace, and taking the steel wire out of the furnace for air cooling.
The structure photograph and plasticity of the M42 steel wire (phi 4.0mm) after the above treatment are shown in FIG. 4, and it can be seen that the average grain size is 4.1 μ M, and the number density of secondary carbides reaches 2.3X 106mm-2Total delay ofThe elongation was about 18.3%. Fig. 9 shows that the quenched and tempered hardness of the M42 steel wire can reach HRC 68.7. Therefore, the heat treatment method can obviously refine the structure of the high-speed steel wire and improve the plasticity and the quenching and tempering hardness of the steel wire.
Example 4:
m2 high speed Steel A1The temperature was about 825 ℃. M2 wire rods with a diameter of 5.5mm were treated as follows:
(1) heating the M2 steel wire to 920 ℃ for 1h, then cooling the steel wire to 500 ℃ in a furnace, then heating the steel wire to 860 ℃ again for 1h, cooling the steel wire to 500 ℃ in the furnace, and taking the steel wire out of the furnace for air cooling.
(2) The M2 steel wire processed above was cold drawn.
(3) Heating the M2 steel wire to 835 ℃, preserving heat for 15min, quickly cooling to 780 ℃, and preserving heat for 20 min; the above operation was repeated 6 times in a cycle.
(4) Heating the M2 steel wire to 550 ℃, and keeping the temperature for 1 h.
(5) Heating the M2 steel wire to 860 ℃, and preserving heat for 4 hours;
(6) And (3) rapidly cooling the steel wire to 740 ℃ at a cooling speed of 5 ℃/min, preserving heat for 5h, cooling the steel wire to 500 ℃ in a furnace, and taking the steel wire out of the furnace for air cooling.
The structure photograph of the M2 steel wire (phi 4.5mm) after the above treatment is shown in FIG. 6, and it can be seen that the average grain size is 4.5 μ M, and the number density of the secondary carbides reaches 1.6X 106mm-2The total elongation was about 19.3%. Fig. 10 shows that the quenched and tempered hardness of the M2 steel wire can reach HRC 65.7. In contrast, the grain size of the M2 steel wire with the same specification produced by the conventional process reaches more than 10 μ M, and the number density of the secondary carbides is less than 1.2 multiplied by 106mm-2The total elongation is less than 12%, and the quenching hardness is about 64 HRC. Therefore, the heat treatment method can obviously refine the structure of the high-speed steel wire and improve the plasticity and the quenching and tempering hardness of the steel wire.
Example 5:
m2 wire rods with a diameter of 5.5mm were treated as follows:
(1) heating the M2 steel wire to 950 ℃ for 30min, cooling the steel wire to 500 ℃ in a furnace, then heating the steel wire to 850 ℃ again for 2h, cooling the steel wire to 500 ℃ in the furnace, and taking the steel wire out of the furnace for air cooling.
(2) The M2 steel wire processed above was cold drawn.
(3) Heating the M2 steel wire to 840 ℃ and preserving heat for 30min, and then quickly cooling to 770 ℃ and preserving heat for 30 min; the above operation was repeated 6 times in a cycle.
(4) Heating the M2 steel wire to 500 ℃, and keeping the temperature for 1 h.
(5) Heating M2 steel wire to 870 ℃, and preserving heat for 3 h;
(6) and (3) rapidly cooling the steel wire to 720 ℃ at a cooling speed of 5 ℃/min, preserving heat for 6 hours, cooling the steel wire to 500 ℃ in a furnace, and taking the steel wire out of the furnace for air cooling.
The structure photograph and plasticity of the treated M2 steel wire (phi 4.3mm) are shown in FIG. 7, and it can be seen that the average grain size is 4.7 μ M, and the number density of the secondary carbides reaches 1.3X 106mm-2The total elongation was about 21.8%. Fig. 10 shows the quenched and tempered hardness of the M2 steel wire, reaching HRC 66. Therefore, the heat treatment method can obviously refine the structure of the high-speed steel wire and improve the plasticity and the quenching and tempering hardness of the steel wire.
Example 6:
m2 wire rods with a diameter of 5.5mm were treated as follows:
(1) heating the M2 steel wire to 970 ℃ for 20min, then cooling the steel wire to 500 ℃ in a furnace, then heating the steel wire to 860 ℃ again for 2h, cooling the steel wire to 500 ℃ in the furnace, and taking the steel wire out of the furnace for air cooling.
(2) The M2 steel wire processed above was cold drawn.
(3) Heating the M2 steel wire to 850 ℃ and preserving heat for 20min, and then quickly cooling to 775 ℃ and preserving heat for 15 min; the operation is circularly carried out for 6 times;
(4) heating the M2 steel wire to 600 ℃, and keeping the temperature for 1 h.
(5) Heating the M2 steel wire to 890 ℃, and preserving heat for 2 h;
(6) and (3) rapidly cooling the steel wire to 750 ℃ at a cooling speed of 10 ℃/min, preserving heat for 4h, cooling the steel wire to 500 ℃ in a furnace, and taking the steel wire out of the furnace for air cooling.
The structure photograph and plasticity of the treated M2 steel wire (phi 4.0mm) are shown in FIG. 8, and it can be seen that the average grain size is 4.3 μ M, and the number density of the secondary carbides reaches 1.9X 106mm-2The total elongation was about 20.2%. FIG. 10 shows the M2 steelThe quenching and tempering hardness of the wire can reach HRC 65.5. Therefore, the heat treatment method can obviously refine the structure of the high-speed steel wire and improve the plasticity and the quenching and tempering hardness of the steel wire.

Claims (1)

1. A processing method of high-speed steel wires is characterized by comprising the following steps: the processing method comprises the following steps: carrying out structure coarsening treatment and cold machining treatment on the high-speed steel wire; carrying out oscillation thinning treatment on the steel wire subjected to cold machining, and then sequentially carrying out alloy clustering treatment, austenitizing treatment and rapid desolventizing treatment to obtain the steel wire;
wherein the structure coarsening treatment comprises two heat treatment steps, namely the first step of carbide coarsening heat treatment, wherein the heating temperature is 900-1000 ℃, and the heating time is 15 min-1 h; secondly, carrying out carbide graining heat treatment at the heating temperature of 830-860 ℃ for 1-2 h;
the steel wire is heated to A by the oscillation thinning treatment1Keeping the temperature above 5-30 ℃ for 15-30 min, and cooling to A1Keeping the temperature below 30-60 ℃ for 15-30 min; and the oscillation refining treatment process is circulated for at least five times;
The clustering treatment temperature of the alloy is 500-600 ℃, and the treatment time is 0.5-1 h;
the austenitizing treatment is to heat the high-speed steel wire to 860-900 ℃ and preserve heat for 2-4 h;
the rapid desolventizing treatment is to cool the steel wire to 720-760 ℃ at a cooling speed of not less than 2 ℃/min, keep the temperature for 2-6 h, cool the furnace to 500 ℃, and cool the furnace;
the high-speed steel wire is M42 steel or M2 steel.
CN202110781924.XA 2021-07-09 2021-07-09 Processing method of high-speed steel wire Active CN113430361B (en)

Priority Applications (1)

Application Number Priority Date Filing Date Title
CN202110781924.XA CN113430361B (en) 2021-07-09 2021-07-09 Processing method of high-speed steel wire

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
CN202110781924.XA CN113430361B (en) 2021-07-09 2021-07-09 Processing method of high-speed steel wire

Publications (2)

Publication Number Publication Date
CN113430361A CN113430361A (en) 2021-09-24
CN113430361B true CN113430361B (en) 2022-06-28

Family

ID=77759879

Family Applications (1)

Application Number Title Priority Date Filing Date
CN202110781924.XA Active CN113430361B (en) 2021-07-09 2021-07-09 Processing method of high-speed steel wire

Country Status (1)

Country Link
CN (1) CN113430361B (en)

Family Cites Families (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN108300843A (en) * 2018-02-06 2018-07-20 江苏健力钢管有限公司 A kind of Steel Pipe For Bearing Quick spheroidizing annealing technology
CN108842043B (en) * 2018-07-18 2020-06-16 东南大学 High-speed steel processing method for obtaining composite grain structure
CN110358894A (en) * 2019-08-22 2019-10-22 中钢集团郑州金属制品研究院有限公司 A kind of spring steel wire crystal grain refinement heat treatment process
CN110846563B (en) * 2019-09-27 2021-08-06 无锡宏达重工股份有限公司 Heat treatment process for grain refinement of X12CrMoWVNbN10-1-1
CN110819781B (en) * 2019-11-06 2021-06-01 东南大学 High-speed steel wire circulation heat treatment method
CN112853065B (en) * 2021-01-06 2022-06-28 东南大学 Heat treatment method for tool and die steel

Also Published As

Publication number Publication date
CN113430361A (en) 2021-09-24

Similar Documents

Publication Publication Date Title
CN110438310B (en) Hot work die steel and heat treatment method thereof
CN111485085B (en) Method for improving grain growth resistance of 18CrNiMo7-6 alloy at 930-950 DEG C
CN108559934B (en) Cryogenic treatment process for TC6 titanium alloy forging
CN107099767B (en) A kind of explosion drill bit heat treatment process
CN103333997A (en) Annealing heat treatment method of H13 die steel
CN111438317A (en) Preparation method for forging and forming high-strength high-toughness β -type titanium alloy forging
CN109852777B (en) H13 die steel and heat treatment process thereof
CN107345267A (en) A kind of high-performance TBM disk cutter Technologies for Heating Processing
CN110819781B (en) High-speed steel wire circulation heat treatment method
CN113430361B (en) Processing method of high-speed steel wire
CN113737106B (en) Die steel for 1500MPa hot stamping part cold trimming punching cutter and preparation method thereof
CN108842043B (en) High-speed steel processing method for obtaining composite grain structure
CN110527817B (en) Heat treatment method for hot-setting tooth bit body
JP5904409B2 (en) Manufacturing method of steel materials for molds with excellent toughness
CN109628713B (en) Spheroidizing annealing method of low-carbon steel
CN108588383B (en) Method for refining grain and primary carbide at edge of stainless steel cutter
CN109628833B (en) Cr-Mo-Si-V cold-work die steel and preparation method thereof
CN115537633B (en) Hot work die steel and production method thereof
CN111172373A (en) Low-carbon steel heat treatment process
CN107574298B (en) A kind of solid waste crusher cutter steel
CN112048678B (en) Annealing softening method of low-alloy ultrahigh-strength steel
CN114438298A (en) High-temperature diffusion method and alloy steel
CN108866299B (en) Forging heat treatment method of Cr12MoV steel
CN108866298B (en) Forging heat treatment process of Cr12MoV steel
KR20130128811A (en) Forging process of fine grain steel

Legal Events

Date Code Title Description
PB01 Publication
PB01 Publication
SE01 Entry into force of request for substantive examination
SE01 Entry into force of request for substantive examination
GR01 Patent grant
GR01 Patent grant