CN114686655B - Rapid spheroidizing annealing method for GCr15 steel - Google Patents
Rapid spheroidizing annealing method for GCr15 steel Download PDFInfo
- Publication number
- CN114686655B CN114686655B CN202210368470.8A CN202210368470A CN114686655B CN 114686655 B CN114686655 B CN 114686655B CN 202210368470 A CN202210368470 A CN 202210368470A CN 114686655 B CN114686655 B CN 114686655B
- Authority
- CN
- China
- Prior art keywords
- spheroidizing annealing
- temperature
- rapid
- gcr15 steel
- spheroidizing
- 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
Links
- 238000000137 annealing Methods 0.000 title claims abstract description 70
- 238000000034 method Methods 0.000 title claims abstract description 70
- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 48
- 239000010959 steel Substances 0.000 title claims abstract description 48
- 238000010438 heat treatment Methods 0.000 claims abstract description 41
- 238000001816 cooling Methods 0.000 claims abstract description 33
- 230000006698 induction Effects 0.000 claims abstract description 23
- 238000004321 preservation Methods 0.000 claims abstract description 16
- 239000000463 material Substances 0.000 claims description 7
- 230000008569 process Effects 0.000 abstract description 53
- 238000005265 energy consumption Methods 0.000 abstract description 14
- 230000000694 effects Effects 0.000 abstract description 6
- 238000010791 quenching Methods 0.000 abstract description 4
- 230000000171 quenching effect Effects 0.000 abstract description 4
- 230000009467 reduction Effects 0.000 abstract description 2
- 230000009466 transformation Effects 0.000 description 13
- 239000002245 particle Substances 0.000 description 10
- 229910001562 pearlite Inorganic materials 0.000 description 10
- 229910001566 austenite Inorganic materials 0.000 description 9
- 229910001563 bainite Inorganic materials 0.000 description 9
- 229910001567 cementite Inorganic materials 0.000 description 8
- KSOKAHYVTMZFBJ-UHFFFAOYSA-N iron;methane Chemical compound C.[Fe].[Fe].[Fe] KSOKAHYVTMZFBJ-UHFFFAOYSA-N 0.000 description 8
- 229910052799 carbon Inorganic materials 0.000 description 5
- 150000001247 metal acetylides Chemical group 0.000 description 5
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 4
- 238000005516 engineering process Methods 0.000 description 4
- 238000004519 manufacturing process Methods 0.000 description 4
- 230000006911 nucleation Effects 0.000 description 4
- 238000010899 nucleation Methods 0.000 description 4
- 238000001556 precipitation Methods 0.000 description 4
- 239000012798 spherical particle Substances 0.000 description 4
- 238000005336 cracking Methods 0.000 description 3
- 230000007547 defect Effects 0.000 description 3
- 238000010586 diagram Methods 0.000 description 3
- 239000007789 gas Substances 0.000 description 3
- 239000010453 quartz Substances 0.000 description 3
- 238000005096 rolling process Methods 0.000 description 3
- VYPSYNLAJGMNEJ-UHFFFAOYSA-N silicon dioxide Inorganic materials O=[Si]=O VYPSYNLAJGMNEJ-UHFFFAOYSA-N 0.000 description 3
- 229910000859 α-Fe Inorganic materials 0.000 description 3
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 2
- 229910045601 alloy Inorganic materials 0.000 description 2
- 239000000956 alloy Substances 0.000 description 2
- 230000015572 biosynthetic process Effects 0.000 description 2
- 230000008859 change Effects 0.000 description 2
- 239000000498 cooling water Substances 0.000 description 2
- 238000005520 cutting process Methods 0.000 description 2
- 238000009826 distribution Methods 0.000 description 2
- 238000011534 incubation Methods 0.000 description 2
- 239000011159 matrix material Substances 0.000 description 2
- 239000002243 precursor Substances 0.000 description 2
- 230000007704 transition Effects 0.000 description 2
- 229910001339 C alloy Inorganic materials 0.000 description 1
- 238000003723 Smelting Methods 0.000 description 1
- 229910001315 Tool steel Inorganic materials 0.000 description 1
- 235000010724 Wisteria floribunda Nutrition 0.000 description 1
- 230000002159 abnormal effect Effects 0.000 description 1
- 238000004220 aggregation Methods 0.000 description 1
- 230000002776 aggregation Effects 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 238000007664 blowing Methods 0.000 description 1
- 239000005539 carbonized material Substances 0.000 description 1
- 229910052804 chromium Inorganic materials 0.000 description 1
- 239000011651 chromium Substances 0.000 description 1
- 230000000052 comparative effect Effects 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 238000000354 decomposition reaction Methods 0.000 description 1
- 238000005098 hot rolling Methods 0.000 description 1
- 238000009776 industrial production Methods 0.000 description 1
- 230000002401 inhibitory effect Effects 0.000 description 1
- 230000014759 maintenance of location Effects 0.000 description 1
- 229910000734 martensite Inorganic materials 0.000 description 1
- 230000007246 mechanism Effects 0.000 description 1
- QMQXDJATSGGYDR-UHFFFAOYSA-N methylidyneiron Chemical compound [C].[Fe] QMQXDJATSGGYDR-UHFFFAOYSA-N 0.000 description 1
- 239000000203 mixture Substances 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 229910052757 nitrogen Inorganic materials 0.000 description 1
- 238000002360 preparation method Methods 0.000 description 1
- 230000001681 protective effect Effects 0.000 description 1
- 238000001073 sample cooling Methods 0.000 description 1
- 238000007493 shaping process Methods 0.000 description 1
- 238000004904 shortening Methods 0.000 description 1
- 238000010583 slow cooling Methods 0.000 description 1
- 239000002436 steel type Substances 0.000 description 1
- 238000006467 substitution reaction Methods 0.000 description 1
- 238000004381 surface treatment Methods 0.000 description 1
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 1
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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/26—Methods of annealing
- C21D1/32—Soft annealing, e.g. spheroidising
-
- 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
- C21D1/34—Methods of heating
- C21D1/42—Induction heating
-
- 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
- C21D6/002—Heat treatment of ferrous alloys containing Cr
-
- 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
-
- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
- Y02P10/00—Technologies related to metal processing
- Y02P10/25—Process efficiency
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 rapid spheroidizing annealing method for GCr15 steel. According to the method, annealed GCr15 steel is directly placed in a Formastor high-frequency induction line device, the temperature rise and the temperature reduction are rapidly completed within 10 seconds, and austenitizing and spheroidizing processes are directly completed in a high-frequency coil, so that the time is greatly shortened; meanwhile, the invention effectively shortens the temperature fluctuation range, shortens the traditional process of normalizing and then spheroidizing annealing, adopts isothermal quenching to obtain a medium-temperature bainitic structure and then spheroidizing annealing, avoids a large amount of temperature raising and lowering processes, and greatly reduces energy consumption. The invention has simple flow, high efficiency and energy saving, and can obviously improve the spheroidizing annealing efficiency of GCr15 steel and improve the spheroidizing annealing effect by adjusting the heat preservation temperature, the heat preservation time and the cooling rate of spheroidizing annealing through high-frequency rapid heating and cooling.
Description
Technical Field
The invention relates to the field of steel, in particular to an online rapid spheroidizing annealing method for a GCr15 bearing steel wire rod.
Background
Bearing steels are an important component of mechanical equipment by virtue of their good toughness and high fatigue and wear resistance. With the continuous progress of technical equipment such as smelting, rolling and heat treatment, the requirements on bearing steel are also continuously increased, and a spheroidizing annealing mode which is one of key links for controlling the quality of carbonized materials is particularly important.
GCr15 steel is a common typical bearing steel, and its original structure is generally lamellar pearlite, which has high hardness, high brittleness, easy cracking and difficult cutting, and thus, spheroidization is often required. The spheroidized structure is a spherical pearlite with slightly lower strength and hardness, but with lower plasticity, machinability and cold formability, and low deformation and cracking tendency during quenching, so that the preparation of the structure is prepared for the subsequent heat treatment. However, the common spheroidizing annealing has a slow cooling speed and a long production period, so that an important problem to be considered is how to shorten the annealing time and reduce the energy consumption in the production practice so as to achieve the purpose of improving the production efficiency. Therefore, how to make the steel product have faster production time, lower energy consumption and better performance is a technical problem to be solved in the field.
At present, a large number of spheroidizing annealing technologies of GCr15 steel, H13 steel, gear steel, cutter steel and other steel types are researched for spheroidizing annealing technology in the steel field, for example, a patent number CN102382962B discloses a rapid spheroidizing annealing process for GCr15 bearing steel pipes, the process is complex, the temperature rise and fall time is long, and the process duration and energy consumption are greatly increased.
The patent No. CN201710411463.0, namely an online rapid spheroidizing annealing method for GCr15 bearing steel after hot rolling, adopts an optimized spheroidizing process, controls the precipitation of proeutectoid carbide in the rolling process in a deformation induction mode, shortens the time required by spheroidizing annealing, and improves the energy efficiency; the method disclosed in CN201810318301.7 patent, namely a rapid spheroidizing annealing process method for GCr15 bearing steel, effectively controls the size of the proeutectoid carbide, and provides more nucleation positions for cementite precipitation in the eutectoid transformation process, thereby effectively shortening the time required by spheroidizing annealing and improving the energy efficiency; the invention of the patent number CN20110354494. X, GCr15 bearing steel tube rapid spheroidizing annealing process, effectively shortens the residence time of a network carbide precipitation interval, achieves the purpose of inhibiting the precipitation of network carbide, can obtain good spheroidizing structure in a short time, and greatly shortens the spheroidizing time. The three rapid spheroidizing annealing processes are only improved in the pearlite spheroidizing annealing process after rolling, but the pearlite spheroidizing annealing process is relatively long in time consumption, and the bearing steel before spheroidizing annealing generally needs to be normalized to room temperature, needs a large amount of heating and cooling, wastes a lot of energy sources and does not fundamentally solve the spheroidizing annealing energy consumption problem.
Disclosure of Invention
The invention aims to provide a rapid spheroidizing annealing method for GCr15 steel, aiming at the problems of the spheroidizing annealing technology of the existing GCr15 steel. According to the method, annealed GCr15 steel is directly placed in a Formastor high-frequency induction line device, the temperature rise and the temperature reduction are rapidly completed within 10 seconds, and austenitizing and spheroidizing processes are directly completed in a high-frequency coil, so that the time is greatly shortened; meanwhile, the invention effectively shortens the temperature fluctuation range, reduces the process of normalizing to eliminate secondary carbide and then spheroidizing annealing in the traditional process, adopts the quenching to obtain a medium-temperature bainitic structure and then spheroidizing annealing, avoids a large number of temperature raising and lowering processes, and greatly reduces the energy consumption, which is also unique in the invention. The invention has simple flow, high efficiency and energy saving, and can obviously improve the spheroidizing annealing efficiency of GCr15 steel and improve the spheroidizing annealing effect by adjusting the heat preservation temperature, the heat preservation time and the cooling rate of spheroidizing annealing through high-frequency rapid heating and cooling.
The technical scheme of the invention is as follows:
a rapid spheroidizing annealing method for GCr15 steel, comprising the steps of: the wire rod of GCr15 steel is placed in a high-frequency induction device to carry out the following operations:
(1) Heating the wire rod to 880-980 ℃ for 5-10 s, and preserving heat at the temperature for 15-30 min until the sample is completely austenitized;
(2) Then the wire is rapidly cooled to 400+/-10 ℃ for 5-10 s, and the temperature is kept for 425-445 s;
(3) Then the wire is quickly heated to 678+/-10 ℃ for 5-10 s, and the temperature is kept for 90-120 s;
(4) The temperature of the wire rod is rapidly reduced to 578+/-10 ℃ for 5-10 s, and then the wire rod is preserved for 50-75 s;
(5) And rapidly cooling the wire rod subjected to heat preservation again to room temperature for 5-10 seconds to finish spheroidizing annealing.
The GCr15 steel comprises the following components in percentage by weight: 0.95-1.10%, si:0.15-0.35%, mn: less than or equal to 0.5 percent, cr:1.30 to 1.60 percent and the balance of Fe.
The high-frequency induction device is a Formastor high-frequency induction device, and the diameter of the GCr15 steel wire rod is 2.5-3.5 mm.
The start temperature of the pearlite to austenite transformation is specifically 628 ℃.
The initial temperature of the transformation from austenite to bainite is 400 ℃.
The invention has the substantial characteristics that:
in the prior art, the conventional spheroidizing annealing process is that normalizing (cooling to room temperature is needed) is carried out first, and then the normalizing is put into an annealing furnace for slow spheroidizing annealing process. The core innovation point of the invention is to combine the two processes, directly place the sample into a high-frequency induction furnace for austenitizing, not perform normalizing (i.e. not need to be cooled to room temperature), directly perform medium-temperature bainite transformation (cooled to about 400 ℃), then rapidly cool to finish heat preservation at two temperatures, and the performance can also meet the related requirements, but greatly reduce the energy consumption. The rapid temperature rise and fall of the process is guaranteed to be realized through a Formastor high-frequency induction device, and the conventional annealing furnace cannot achieve the rapid temperature rise and fall.
The mechanism is that the conventional spheroidizing annealing process comprises the following steps: the secondary carbides are broken up by normalizing, then partially fused into austenite by long-time annealing and heat preservation, a considerable amount of undissolved carbides remain, and during the subsequent cooling process, carbides are precipitated with these residual carbides as cores.
And (3) a rapid annealing process: a certain amount of undissolved carbide is obtained directly through bainite transformation with short energy consumption (no cooling to room temperature and little energy is needed), then a small amount of secondary carbide is crushed through isothermal temperature at a first rapid temperature, and carbide is precipitated by taking undissolved carbide as a core at a second rapid temperature, so that the same performance can be realized.
The other innovation point of the invention is that the material is selected as a wire, and the time of the heat treatment process is controlled by the moving speed of the wire in the induction coil; secondly, the high-frequency induction coil and the rapid cooling can be combined with two procedures of the conventional process, so that the use and the time of equipment are greatly reduced.
The beneficial effects of the invention are as follows:
according to the technical scheme, the GCr15 steel rapid spheroidizing annealing process is implemented through the high-frequency induction rapid heating and steam/water rapid cooling channels, so that carbide is spheroidized on line, the time of the whole process is only about 0.5h, the spheroidizing annealing period is greatly shortened, the energy consumption is greatly reduced, the carbide is uniformly distributed, carbide aggregation is avoided, carbide particles are tiny, the process is simple, the principle is clear, and the industrial production is facilitated.
The invention overcomes the defects that furnace body equipment in the prior art needs more electric energy and damages equipment through repeated high and low temperature circulation, skillfully utilizes precursor treatment (the differences are mentioned), saves electric energy, shortens heat treatment time and achieves the same effect; not only is less time needed (as can be seen from process comparisons), less electrical energy is needed, and a ton of product can save about 100kWh.
Drawings
FIG. 1 is a schematic diagram of the specific process described in the present invention.
FIG. 2 is a schematic diagram of the apparatus for applying the process of the present invention (1. Quartz tube, 2. Gas tube, 3. Cooling water tube, 4. Sample, 5. Thermocouple, 6. High frequency induction coil).
FIG. 3 shows the metallographic structure of the sample before the processing in all examples.
FIG. 4 metallographic structure of the sample after the process of example 4.
The specific embodiment is as follows:
the present invention will be further specifically described below by way of specific examples with reference to the accompanying drawings. An on-line rapid spheroidizing annealing process for GCr15 carbon tool steel is shown in figure 1. Fig. 2 shows a schematic diagram of an application device (high frequency induction device) of the process according to the invention. The sample 4 is placed in the quartz tube 1, and the quartz tube 1 surrounds the gas tube 2, the cooling water tube 3 and the high-frequency induction coil 6 in this order, and the temperature of the sample is collected by the thermocouple 5. When the sample is heated, the purpose of rapid sample heating is achieved through heating of the high-frequency induction coil 6, and the purpose of rapid sample cooling is achieved through blowing the protective gas nitrogen through the air pipe 2. FIG. 3 shows the metallographic structure of the sample before the process treatment according to the invention. The original microstructure of GCr15 before rapid spheroidization was lamellar pearlite.
The spheroidizing annealing high-frequency induction device in the embodiment of the invention is a formalter-II type full-automatic phase change expander of Fuji electric wave engineering machine Co., ltd., hereinafter referred to as a formalstor high-frequency induction device. The device can realize the quick heating up of material, also can make the quick cooling down of material.
The device used for observing the metallographic microstructure in the embodiment of the invention is an Olympus metallographic microscope.
The national standard adopted for measuring the spheroidization grade in the embodiment of the invention is a rating method in GB/T18254-2016 high-carbon chromium bearing steel.
The present invention will be described in more detail below with reference to the accompanying drawings. Through the GCr15 rapid spheroidizing annealing process shown in fig. 4, the microstructure after heat treatment is that tiny and uniform spherical carbides are dispersed and distributed on a ferrite matrix.
The rapid spheroidizing annealing process of the GCr15 bearing steel is shown in figure 1, and specifically comprises rapid heating, heat preservation, rapid cooling, heat preservation above Ac1 and Ac 1 The following steps are kept warm and quickly cooled to room temperature:
1. a rapid temperature rise process and a heat preservation process. The most basic problem of spheroidizing annealing is how to solve the problem of forming granular carbide cores, wherein granular carbide in a structure is formed by growing residual carbide particles during heating austenitizing, and the more the residual carbide particles are, the easier the complete spheroidizing structure is obtained, so that specific requirements for heating austenitizing are required during spheroidizing. In addition to requiring the retention of as many remaining carbide particles as possible during austenitization, austenite having as large a carbon concentration as possible is obtained, the non-uniformity of the austenite composition favors nucleation and growth processes of pearlite transformation, and undissolved carbide particles can become non-uniform nucleation centers of pearlite transformation, thereby enabling the abnormal decomposition rate of supercooled austenite to be 6 to 7 times faster than that of uniform austenite. A rapid temperature rise to a suitable temperature and a short incubation time are therefore required for the austenitizing stage. The invention adopts 10s to quickly raise the temperature to 980 ℃, and the temperature is kept for 20min.
2. Rapidly cooling to a bainite transformation region. Before spheroidizing hypereutectoid steel, the netlike carbide needs to be eliminated, and generally, a quenching or normalizing process is adopted to eliminate the netlike carbide distributed in chain shape along the grain boundary. The invention only reduces to the bainite region with medium temperature, thereby achieving the effect of evenly distributing carbide. The invention keeps warm at the bainite starting transition temperature (400 ℃) for 435s.
3. Rapid cooling Ac 1 The heat is preserved. The process of rapid cooling increases the non-uniformity of austenite components and simultaneously retains more undissolved carbide particles, and proper heat preservation can promote the remarkable increase of crystal defects and structural non-uniformity, and the residual carbide particles are more dispersed and finer. The invention keeps the temperature above Ac1 (678 ℃) for 102s.
4. Rapid cooling Ac 1 The following was kept warm. In the temperature range, carbide tissues can be precipitated at the position with high linear defect density, dispersed granular carbide is formed in a part of the area, finally, spheroidized tissues are formed, and the formed carbide particles are small in size, round and uniform in appearance and dispersed. The invention is characterized in Ac 1 The following (578 ℃ C.) was incubated for 60s.
5. Rapidly cooled to room temperature. The key point of the rapid spheroidizing annealing process for GCr15 bearing steel provided by the invention is to select a proper heat treatment process, heating temperature and heat preservation time, the process can greatly shorten the spheroidizing annealing period, save energy consumption and obtain the structure of carbide particles which are dispersed and distributed on a ferrite matrix, wherein the carbide particles are small, uniform and round, and the hardness is 28HRC. The invention can ensure that the processed workpiece has good shaping processability and cutting performance, thereby improving the quality and the service performance of the product.
Example 1
(1) The GCr15 steel is selected as a wire rod with the diameter of 3mm, and comprises the following components in percentage by weight: 0.95-1.10%, si:0.15-0.35%, mn: less than or equal to 0.5 percent, cr:1.30 to 1.60 percent and the balance of Fe.
(2) Rapidly heating (10 s) to 680 ℃, and preserving heat for 20min at the temperature until the sample is completely austenitized;
(3) Rapidly cooling (5 s) to 400 ℃, and preserving heat for 435s;
(4) Rapidly heating (5 s) to 678 ℃, and preserving heat for 102s;
(5) Rapidly cooling (5 s) to 578 ℃, and preserving heat for 60s;
(6) And cooling to room temperature for 10 seconds to finish spheroidizing annealing.
Through the above comprehensive control, part of carbide obtained after spheroidizing annealing is in a spherical particle shape, part of carbide is lamellar pearlite, the distribution is uneven, a large number of network cementite areas appear, and the grade is 5.
Example 2
(1) The GCr15 steel is selected as a wire rod with the diameter of 3mm, and comprises the following components in percentage by weight: 0.95-1.10%, si:0.15-0.35%, mn: less than or equal to 0.5 percent, cr:1.30 to 1.60 percent and the balance of Fe.
(2) Rapidly heating (10 s) to 980 ℃, and preserving heat for 20min at the temperature until the sample is completely austenitized;
(3) Rapidly cooling (5 s) to room temperature;
(4) After the sample is cooled to room temperature, rapidly heating (5 s) to 678 ℃, and preserving heat for 102s;
(5) Rapidly cooling (5 s) to 578 ℃, and preserving heat for 60s;
(6) And cooling to room temperature for 10 seconds to finish spheroidizing annealing.
Through the comprehensive control, the obtained carbide after spheroidizing annealing is uniformly distributed in a spherical particle shape, no massive cementite area appears, and the grade is 3. But adds to the energy consumption and time intangibly.
Example 3
(1) The GCr15 steel is selected as a wire rod with the diameter of 3mm, and comprises the following components in percentage by weight: 0.95-1.10%, si:0.15-0.35%, mn: less than or equal to 0.5 percent, cr:1.30 to 1.60 percent and the balance of Fe.
(2) Rapidly heating (10 s) to 980 ℃, and preserving heat for 20min at the temperature until the sample is completely austenitized;
(3) Rapidly cooling (5 s) to 400 ℃, and preserving heat for 435s;
(4) Rapidly heating (5 s) to 678 ℃, and preserving heat for 300s;
(5) Rapidly cooling (5 s) to 578 ℃, and preserving heat for 60s;
(6) And cooling to room temperature for 10 seconds to finish spheroidizing annealing.
Through the comprehensive control, the obtained carbide after spheroidizing annealing is uniformly distributed in a spherical particle shape, no massive cementite area appears, and the grade is 4. The second time of heat preservation is too long.
Example 4
(1) The GCr15 steel is selected as a wire rod with the diameter of 3mm, and comprises the following components in percentage by weight: 0.95-1.10%, si:0.15-0.35%, mn: less than or equal to 0.5 percent, cr:1.30 to 1.60 percent and the balance of Fe.
(2) Rapidly heating (10 s) to 980 ℃, and preserving heat for 20min at the temperature until the sample is completely austenitized;
(3) Rapidly cooling (5 s) to 400 ℃, and preserving heat for 435s;
(4) Rapidly heating (5 s) to 678 ℃, and preserving heat for 102s;
(5) Rapidly cooling (5 s) to 578 ℃, and preserving heat for 60s;
(6) And cooling to room temperature for 10 seconds to finish spheroidizing annealing.
By the above comprehensive control, the metallographic photograph of the sample obtained in this example is shown in fig. 4, and it can be seen from the photograph that the obtained carbide after spheroidizing annealing is uniformly distributed in the form of spherical particles, and no large cementite region appears, and the grade is 2. And the process time is the shortest.
The rapid temperature rise to the fully austenitic region is critical to ensure the later complete bainitic or martensitic transformation, and if not fully austenitized, the formation of the network cementite region (example 1) is easily caused, and the network cementite cannot be eliminated in the later spheroidizing annealing, and can be brought into the later product, the network cementite is a main cause of cracking of the material in the later use of the material. The patent skillfully uses the precursor carbide (both the example 3 and the example 4 are available) for forming the pearlescence, and provides a precondition for the formation of the spherical pearlescence in the later period. Examples 3 and 4 samples were austenitized without normalizing (i.e., without cooling to room temperature), and directly subjected to medium temperature bainitic transformation (cooling to about 400 degrees), avoiding repeated heating of the samples to the equipment (example 2), and reducing energy consumption. Although proper incubation in the bainite region increases time (example 4), long waiting times and energy losses to bring down the room temperature sample toward complete equilibrium are avoided (example 2). Example 3 is that complete transformation of bainite is completed, fracture of carbide is completed, and energy consumption is only increased if transformation time is increased additionally.
According to the invention, the carbide in the lamellar spherical pearlite in an original annealed state is rapidly broken and dissolved and a fine spherical carbide nucleation core is separated out by adopting rapid induction heating and short-time heating/heat preservation, and rapid cooling is carried out to a bainite region in a medium-temperature transition region, so that the spheroidizing process is completed for the short-time heat preservation of two subsequent temperature periods. The short-time rapid induction heating treatment shortens the spheroidizing annealing time of the GCr15 steel, improves the spheroidizing rate, greatly reduces the energy consumption, and has finer and more uniform carbide size and distribution than that of the conventional spheroidizing annealing heat treatment.
The parameters of the GCr15 spheroidizing annealing heat treatment process and the comparative spheroidizing annealing heat treatment process are shown in Table 1.
TABLE 1 comparison of the spheroidizing annealing heat treatment process of the present invention with the conventional spheroidizing annealing heat treatment process parameters
From the above examples we can see that GCr15 steel can only be bar material in order to control the temperature rise and drop speed; the diameter of the bar cannot be too large; the diameter is too large (more than 3.5 mm), the rapid short-time induction heating can only achieve the effect of surface treatment, and the heat treatment effect can not be achieved on the sample core tissue, so that the sample tissue is unevenly distributed.
The line Ac1 in FIG. 1, also called eutectoid line, means that when an iron-carbon alloy containing 0.77% -2.11% carbon is cooled to this line, eutectoid transformation, A, occurs at a constant temperature of 727 DEG C 0.77％ →F 0.0218％ +Fe 3 C. Ac3 is the final temperature at which ferrite is transformed into austenite upon heating. The AC1 and AC3 of the alloy are changed due to the difference of carbon content and the change of alloy elements, and the heat treatment temperatureTypically between AC1 and AC3, and thus the heat treatment temperature is changed, the process also needs to be re-studied.
The present invention is not limited to the above-mentioned embodiments, and any equivalent substitutions or modifications according to the scope of the present invention are within the scope of the present invention.
The invention is not a matter of the known technology.
Claims (4)
1. A GCr15 steel rapid spheroidizing annealing method is characterized by comprising the following steps: the wire rod of GCr15 steel is placed in a high-frequency induction device to carry out the following operations:
(1) Heating the bar material to 880-980 ℃ for 5-10 s, and preserving heat for 15-30 min at the temperature until the sample is completely austenitized;
(2) Then the wire is rapidly cooled to 400+/-10 ℃ for 5-10 s, and the temperature is kept for 425-445 s;
(3) Then the wire is quickly heated to 678+/-10 ℃ for 5-10 s, and the temperature is kept for 90-120 s;
(4) The temperature of the wire rod is rapidly reduced to 578+/-10 ℃ for 5-10 s, and then the wire rod is preserved for 50-75 s;
(5) And rapidly cooling the wire rod subjected to heat preservation again to room temperature for 5-10 seconds to finish spheroidizing annealing.
2. The rapid spheroidizing annealing method of GCr15 steel according to claim 1, wherein the GCr15 steel comprises the following components in percentage by weight: 0.95-1.10%, si:0.15-0.35%, mn: less than or equal to 0.5 percent, cr:1.30 to 1.60 percent and the balance of Fe.
3. The rapid spheroidizing annealing method of GCr15 steel according to claim 1, wherein said high frequency induction device is a Formastor high frequency induction device.
4. The rapid spheroidizing annealing method of GCr15 steel according to claim 1, wherein the diameter of the GCr15 steel wire rod is 2.5-3.5 mm.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202210368470.8A CN114686655B (en) | 2022-04-06 | 2022-04-06 | Rapid spheroidizing annealing method for GCr15 steel |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202210368470.8A CN114686655B (en) | 2022-04-06 | 2022-04-06 | Rapid spheroidizing annealing method for GCr15 steel |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN114686655A CN114686655A (en) | 2022-07-01 |
| CN114686655B true CN114686655B (en) | 2023-12-08 |
Family
ID=82142242
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN202210368470.8A Active CN114686655B (en) | 2022-04-06 | 2022-04-06 | Rapid spheroidizing annealing method for GCr15 steel |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN114686655B (en) |
Citations (9)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH11201168A (en) * | 1998-01-12 | 1999-07-27 | Nippon Seiko Kk | Rolling bearing |
| CN104328259A (en) * | 2014-10-13 | 2015-02-04 | 北京科技大学 | GCr15 high carbon chromium bearing steel on-line rapid spheroidizing annealing technology |
| JP2015089960A (en) * | 2013-11-07 | 2015-05-11 | 株式会社ジェイテクト | Method of manufacturing rough shape material of rolling shaft bearing |
| CN104662192A (en) * | 2012-09-26 | 2015-05-27 | Skf公司 | Hypoeutectoid bearing steel |
| CN104805258A (en) * | 2014-06-27 | 2015-07-29 | 河北工程大学 | 42CrMo steel fast spheroidizing annealing method |
| JP2016037631A (en) * | 2014-08-07 | 2016-03-22 | 高周波熱錬株式会社 | Rapid softening annealing treatment method for carbon steel |
| CN106191396A (en) * | 2016-08-16 | 2016-12-07 | 武汉钢铁股份有限公司 | Cold formability 65Mn hot rolled steel plate Fast Spheroidizing Annealing method |
| JP2017214621A (en) * | 2016-05-31 | 2017-12-07 | 株式会社神戸製鋼所 | Manufacturing method of hyper-eutectoid steel wire |
| CN109913622A (en) * | 2019-04-12 | 2019-06-21 | 河北工业大学 | A kind of T8 carbon tool steel Fast Spheroidizing Annealing method |
Family Cites Families (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP6703385B2 (en) * | 2015-09-18 | 2020-06-03 | 国立大学法人大阪大学 | Steel with high hardness and excellent toughness |
-
2022
- 2022-04-06 CN CN202210368470.8A patent/CN114686655B/en active Active
Patent Citations (9)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH11201168A (en) * | 1998-01-12 | 1999-07-27 | Nippon Seiko Kk | Rolling bearing |
| CN104662192A (en) * | 2012-09-26 | 2015-05-27 | Skf公司 | Hypoeutectoid bearing steel |
| JP2015089960A (en) * | 2013-11-07 | 2015-05-11 | 株式会社ジェイテクト | Method of manufacturing rough shape material of rolling shaft bearing |
| CN104805258A (en) * | 2014-06-27 | 2015-07-29 | 河北工程大学 | 42CrMo steel fast spheroidizing annealing method |
| JP2016037631A (en) * | 2014-08-07 | 2016-03-22 | 高周波熱錬株式会社 | Rapid softening annealing treatment method for carbon steel |
| CN104328259A (en) * | 2014-10-13 | 2015-02-04 | 北京科技大学 | GCr15 high carbon chromium bearing steel on-line rapid spheroidizing annealing technology |
| JP2017214621A (en) * | 2016-05-31 | 2017-12-07 | 株式会社神戸製鋼所 | Manufacturing method of hyper-eutectoid steel wire |
| CN106191396A (en) * | 2016-08-16 | 2016-12-07 | 武汉钢铁股份有限公司 | Cold formability 65Mn hot rolled steel plate Fast Spheroidizing Annealing method |
| CN109913622A (en) * | 2019-04-12 | 2019-06-21 | 河北工业大学 | A kind of T8 carbon tool steel Fast Spheroidizing Annealing method |
Non-Patent Citations (2)
| Title |
|---|
| GCr15轴承钢棒线材的球化退火;江运宏;周靖;;热处理(第03期);全文 * |
| GCr15钢的快速球化退火工艺;汪东红;杨霄;陈其伟;朱国辉;;安徽工业大学学报(自然科学版)(第03期);全文 * |
Also Published As
| Publication number | Publication date |
|---|---|
| CN114686655A (en) | 2022-07-01 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN104328259B (en) | GCr15 high carbon chromium bearing steel on-line rapid spheroidizing annealing technology | |
| CN103866095B (en) | A kind of spheroidizing method for being directed to Cr, Mo steel with sheet microstructure | |
| WO2021022542A1 (en) | Preparation method for gcr15 bearing steel by rolling-isothermal spheroidizing annealing treatment | |
| CN105925909B (en) | A kind of bearing steel wire rod and its production method | |
| CN118166286B (en) | 10.9-Grade non-adjustable cold heading steel hot rolled wire rod and manufacturing method thereof | |
| CN118166189B (en) | 12.9-Grade annealing-free hot-rolled complex-phase cold heading steel wire rod and manufacturing method thereof | |
| CN104805258A (en) | 42CrMo steel fast spheroidizing annealing method | |
| CN113957209A (en) | High-carbon chromium bearing steel high-intensity magnetic field rapid spheroidizing annealing process | |
| CN109182680B (en) | Method for controlling annealing hardness of martensitic stainless steel rod wire for cold heading | |
| CN101319270B (en) | Thermal treatment method for improving mechanical performances of normalized steel plate | |
| CN108085591A (en) | A kind of steel plate HTNM400 and its production method with low-welding crack-sensitive energy | |
| CN114107626A (en) | Continuous spheroidizing annealing method for high-carbon chromium bearing steel round steel | |
| CN101660036A (en) | Heat treating method of high strength and high ductility steel tube | |
| CN105369015A (en) | 42 CrMo shaft part quenching and heat-treatment technology | |
| WO2023246950A1 (en) | Spring steel and spheroidizing annealing method therefor | |
| Wu et al. | Effect of initial spheroidizing microstructure after quenching and tempering on wear and contact fatigue properties of GCr15 bearing steel | |
| CN107058692B (en) | A kind of online Fast Spheroidizing Annealing method after GCr15 bearing steels hot rolling | |
| CN118207405A (en) | 10.9-Grade high Cr annealing-free cold heading steel hot rolled wire rod and manufacturing method thereof | |
| CN104532139B (en) | High-strength tenacity steel ball and production method thereof | |
| CN104745787B (en) | Production method of tool steel capable of being directly cold rolled | |
| CN103320686B (en) | Cold rolled sheet No. 45 steel and production method thereof | |
| CN114686655B (en) | Rapid spheroidizing annealing method for GCr15 steel | |
| CN109837367B (en) | Heat treatment process for refining M-A island in granular bainite structure of low-carbon low-alloy steel | |
| CN109913622B (en) | Rapid spheroidizing annealing method for T8 carbon tool steel | |
| CN114717393A (en) | Rapid isothermal spheroidizing annealing method for 42CrMoA steel bar |
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 |