CN110468263A - A kind for the treatment of process obtaining the advanced high-strength steel of high-strength and high ductility - Google Patents
A kind for the treatment of process obtaining the advanced high-strength steel of high-strength and high ductility Download PDFInfo
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- CN110468263A CN110468263A CN201910863208.9A CN201910863208A CN110468263A CN 110468263 A CN110468263 A CN 110468263A CN 201910863208 A CN201910863208 A CN 201910863208A CN 110468263 A CN110468263 A CN 110468263A
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- 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
-
- 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
- C21D6/005—Heat treatment of ferrous alloys containing Mn
-
- 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
- C21D6/008—Heat treatment of ferrous alloys containing Si
Abstract
The invention discloses a kind for the treatment of process for obtaining the advanced high-strength steel of high-strength and high ductility, which is: Steel material is heated to Ae3On 10 DEG C~300 DEG C of austenitizing temperature, and 1min~120min is kept the temperature under above-mentioned austenitizing temperature, perlitic transformation temperature range will be down to by the Steel material of austenitizing: 470 DEG C~700 DEG C, heat preservation 0.1h~6h obtains complete pearlitic structrure, then cools to room temperature；Then, Steel material is heated to Ae3On 1 DEG C~50 DEG C, keep the temperature 1s~300s, the Steel material is set to carry out the inverse austenitizing changed from processing from pearlite to austenite, finally 150 DEG C~500 DEG C of tempering temperature will be heated to 30 DEG C/s~100 DEG C/s heating rate by inverse austenitizing treated Steel material, keeps the temperature and room temperature is down to 50 DEG C/s~200 DEG C/s rate of temperature fall after 10s~300s.Treatment process of the invention makes Steel material under the premise of with very high strong plasticity, is remarkably improved the fracture toughness of Steel material.
Description
Technical field
The present invention relates to material treatment processes technical field more particularly to a kind of places for obtaining the advanced high-strength steel of high-strength and high ductility
Science and engineering skill.
Background technique
The presence of austenite in steel will cause phase change induction plasticity (TRIP) effect, hinder crack propagation effect and absorption
The generation of dislocation effect, and can be used as " hydrogen trap ", these effects hinder crack initiation and propagation, to improve steel material
Wearability, anti-contact fatigue and anti-delayed fracture performance, improve the performance of steel.It is opened by the TRIP effect of retained austenite
It is a trend that sending out, which has the advanced high-strength steel of high-intensitive and good plasticity,.But the content of retained austenite, stability, shape
State, size etc. drastically influence the mechanical property of Steel material, even if under the stress of very little geneva occurs for unstable austenite
The extension of micro-crack in steel is accelerated in body phase transformation；And large-sized blocky retained austenite cognition is easy to crackle along its brittle cracking,
Influence the mechanical property of steel.
For example, the quenching-in third generation high-strength steel matches division technique (quenching&partitioning, Q&P), quenches
Fire-partition-tempering process (quenching-partitioning-tempering, Q-P-T) and quenching-partition-deep cooling-tempering
Technique (Quenching-Partitioning-Cryogenic-Tempering, Q-P-C-T).Wherein, QP (Quenching
And Partitioning) technological principle of steel is when steel being heated to austenitizing area (or two-phase section) constant temperature to keep the temperature one section
Between after, the hardening heat being cooled fast between Ms (martensite start temperature) and Mf (martensitic traoformation terminates temperature) and guarantor
Temperature, generates suitable martensite, is then warming up to the partition temperature higher than Ms temperature, and constant temperature is for a period of time, makes carbon from satiety
(diffusion) is distributed in the martensite of sum into austenite, the enrichment of C element allows a certain amount of austenite in room temperature
Under be stabilized.Q-P-T and Q-P-C-T technique is then on the basis of Q&P technique, respectively by increasing step tempering and deep cooling
Processing processing, in order to obtain more more stable retained austenite body tissues.However, although steel pass through Q&P, Q-P-T
Or after Q-P-C-T process, the strong plasticity of material is obviously improved, but there is the generation of crackle in practical forming process but when,
I.e. fracture toughness is poor.Such as in quenching-partition Q&P steel (quenching-partitioning), although passing through regulation retained austenite
The stability of family name's body makes strength and ductility product be up to 30000MPa%, but fracture toughness is very low, this is because crack tip
Blocky retained austenite be quickly converted to martensite and form brittle martensite chain, crackle is crisp along blocky retained austenite
Property cracking, be greatly lowered so as to cause fracture toughness.Research finds that blocky retained austenite reduces the fracture toughness of material, and
Sheet retained austenite is conducive to improve material fracture toughness, therefore, advanced to improve under the premise of guaranteeing certain plasticity
Crack propagation ability is resisted in the raising of the fracture toughness of high-strength steel, needs to reduce the volume point of blocky retained austenite as far as possible
Number, while increasing the volume fraction of sheet retained austenite.Thus it is necessary to further improve the form of retained austenite, size
With stability to improve steel material obdurability.
Summary of the invention
The purpose of the present invention is to solve the preparation processes that tradition improves Steel Properties, and there are have to split during formed product
Line generates, the problem of fracture toughness difference, and provides a kind of kind of the treatment process for obtaining the advanced high-strength steel of high-strength and high ductility.
What the purpose of the present invention was mainly realized by inverse three treatment process of austenitizing-tempering of pearlite-, specifically
Technical solution is as follows:
A kind for the treatment of process of advanced high-strength steel of acquisition high-strength and high ductility of the invention, comprising the following steps:
1) pearliteization is handled: Steel material is heated to Ae3On 10 DEG C~300 DEG C of austenitizing temperature, and upper
Heat preservation 1min~120min under austenitizing temperature is stated, perlitic transformation humidity province will be down to by the Steel material of austenitizing
Between: 470 DEG C~700 DEG C, heat preservation 0.1h~6h obtains complete pearlitic structrure, then cools to room temperature, wherein Ae3It is described
Ferrite is completely converted into the finishing temperature of austenite in Steel material；
2) inverse austenitizing is handled: will be again heated to Ae by the Steel material of pearliteization processing3On 1 DEG C~50
DEG C, 1s~300s is kept the temperature, so that the Steel material is carried out the inverse austenitizing changed from processing from pearlite to austenite, then quenches
To room temperature；
3) tempering: will be by inverse austenitizing treated Steel material with 30 DEG C/s~100 DEG C/s heating rate
It is heated to 150 DEG C~500 DEG C of tempering temperature, keeps the temperature and room is down to 50 DEG C/s~200 DEG C/s rate of temperature fall after 10s~300s
Temperature.
The treatment process is suitable for inclusion in the Steel material of carbon and manganese element.
Further, before the 1) step carries out pearlite, Homogenization Treatments first can be carried out to Steel material.
Further, before the 1) step carries out pearlite, can first Steel material be rolled or is forged.
Further, the heating rate of heating is 30 DEG C/s~100 DEG C/s when carrying out austenitizing in the 1) step.
Further, the Steel material in the 1) step by austenitizing is down to the cooling speed of perlitic transformation temperature range
Rate is 10 DEG C/s~50 DEG C/s.
Further, the rate of temperature fall that will be down to room temperature by the Steel material of complete pearlite in the 1) step is 30
DEG C/s~100 DEG C/s.
Further, the heating rate heated when carrying out inverse austenitizing in the 2) step is 30 DEG C/s~100 DEG C/s；It quenches
The rate of temperature fall of fire to room temperature is 50 DEG C/s~200 DEG C/s.
Beneficial effect
After the treatment process of above-mentioned steel material passes through pearlite, inverse austenitizing is arranged once to handle before being tempered, by
It can be enriched at cementite in pearlite stage Mn element and C element, austenite inherits in inverse austenitization
The chemical pattern of high carbon content and manganese content at former cementite makes the overcooling austenite after cooling down at this at room temperature with sheet
Form stable is there are highly beneficial, and former ferrite carbon content and manganese content are lower, and overcooling austenite is poor in room temperature stability
And be transformed into martensite, then form sheet retained austenite and lamellar martensite and overlap tissue, it is subsequent can be by tempering at
Reason softens quenched martensite and stablizes remaining residual austenite cognition further, is conducive to the promotion of performance, the treatment process
It can make steel material under the premise of with very high strong plasticity under the premise of reducing process time and cost significantly, it can be significant
Improve the fracture toughness of steel material.
Detailed description of the invention
Fig. 1 is the route map for the treatment of process of the present invention；
Fig. 2 is that step 4 against austenitizing treated sample carries out the diffraction pattern that XRD is tested in embodiment 1；
Fig. 3 is that the sample in Examples 1 to 3 after step 5 tempering carries out the diffraction pattern that XRD is tested respectively；
Fig. 4 is that the SEM of step 4 against sample after austenitizing processing in embodiment 1 schemes；
Fig. 5 is the SEM figure of sample after 2 step 5 tempering of embodiment；
Fig. 6 be in embodiment 1 step 4 against austenitizing processing after sample TEM light field figure；
Fig. 7 be in embodiment 1 step 4 against austenitizing processing after sample TEM dark field plot；
Fig. 8 is the TEM light field figure of sample after step 5 tempering in embodiment 1；
Fig. 9 is the TEM dark field plot in embodiment 1 after step 5 tempering；
Figure 10 is that the finally obtained Steel material of Examples 1 to 4 carries out the stretching that stretching mechanical property testing obtains respectively and answers
Stress-strain curve.
Specific embodiment
The contents of the present invention are further described with reference to the accompanying drawings and examples.
Embodiment 1
High-strength and high ductility processing is carried out for certain model Steel material, the chemical component of the Steel material are as follows: Mn:3.66%, C:
0.41%, Si:0.2%, remaining is iron and inevitable impurity element, and ferrite is completely converted into austenite in the Steel material
Finishing temperature be 718 DEG C, the route map for the treatment of process is as shown in Figure 1, specific processing step is as follows:
1) melted steel material is heated to 1250 DEG C, soaking time carries out Homogenization Treatments for 24 hours.
2) then, the steel ingot after Homogenization Treatments is rolled, is beginning to roll 25% deformation of rolling at temperature is 950 DEG C
Amount rolls 25% deflection at being 850 DEG C in rolling temperature, rolls 25% deflection at being 650 DEG C in finishing temperature, then exists
It is cooled to room temperature in air, obtains rolling rear sample.
3) pearliteization is handled: steel material is heated to 840 DEG C and is kept the temperature 5min carry out with the heating rate of 30 DEG C/s
Then complete austenitizing is cooled at 575 DEG C of medium temperature of perlitic transformation temperature range with the rate of temperature fall of 30 DEG C/s
It keeps the temperature 2h and carries out complete pearlite, room temperature is then down to the rate of temperature fall of 30 DEG C/s.
4) inverse austenitizing is handled: steel material being heated to 750 DEG C with the heating rate of 100 DEG C/s, heat preservation 7s is carried out
Inverse austenitizing is handled, and is then quenched to room temperature with the rate of temperature fall of 100 DEG C/s.
5) 300 DEG C will be heated to the heating rate of 100 DEG C/s, and keep the temperature 60s and carries out tempering, then with 100K/s
Rate of temperature fall fast cooling to room temperature.
Embodiment 2
High-strength and high ductility processing is carried out for certain model Steel material, the chemical component of the Steel material are as follows: Mn:3.66%, C:
0.41%, Si:0.2%, remaining is iron and inevitable impurity element, and ferrite is completely converted into austenite in the Steel material
Finishing temperature be 718 DEG C, the route map for the treatment of process is as shown in Figure 1, specific processing step is as follows:
1) melted steel material is heated to 1250 DEG C, soaking time carries out Homogenization Treatments for 24 hours.
2) then, the steel ingot after Homogenization Treatments is rolled, is beginning to roll 25% deformation of rolling at temperature is 950 DEG C
Amount rolls 25% deflection at being 850 DEG C in rolling temperature, rolls 25% deflection at being 650 DEG C in finishing temperature, then exists
It is cooled to room temperature in air, obtains rolling rear sample.
3) pearliteization is handled: steel material is heated to 840 DEG C and is kept the temperature 5min carry out with the heating rate of 30 DEG C/s
Then complete austenitizing is cooled at 575 DEG C of medium temperature of perlitic transformation temperature range with the rate of temperature fall of 30 DEG C/s
It keeps the temperature 2h and carries out complete pearlite, room temperature is then down to the rate of temperature fall of 30 DEG C/s.
4) inverse austenitizing is handled: steel material being heated to 750 DEG C with the heating rate of 100 DEG C/s, heat preservation 7s is carried out
Inverse austenitizing is handled, and is then quenched to room temperature with the rate of temperature fall of 100 DEG C/s.
5) 400 DEG C will be heated to the heating rate of 100 DEG C/s, and keep the temperature 60s carry out tempering, then with 100 DEG C/
The rate of temperature fall fast cooling of s is to room temperature.
Embodiment 3
High-strength and high ductility processing is carried out for certain model Steel material, the chemical component of the Steel material are as follows: Mn:3.66%, C:
0.41%, Si:0.2%, remaining is iron and inevitable impurity element, and ferrite is completely converted into austenite in the Steel material
Finishing temperature be 718 DEG C, the route map for the treatment of process is as shown in Figure 1, specific processing step is as follows:
1) melted steel material is heated to 1250 DEG C, soaking time carries out Homogenization Treatments for 24 hours.
2) then, the steel ingot after Homogenization Treatments is rolled, is beginning to roll 25% deformation of rolling at temperature is 950 DEG C
Amount rolls 25% deflection at being 850 DEG C in rolling temperature, rolls 25% deflection at being 650 DEG C in finishing temperature, then exists
It is cooled to room temperature in air, obtains rolling rear sample.
3) pearliteization is handled: steel material is heated to 840 DEG C and is kept the temperature 5min carry out with the heating rate of 30 DEG C/s
Then complete austenitizing is cooled at 575 DEG C of medium temperature of perlitic transformation temperature range with the rate of temperature fall of 30 DEG C/s
It keeps the temperature 2h and carries out complete pearlite, room temperature is then down to the rate of temperature fall of 30 DEG C/s.
4) inverse austenitizing is handled: steel material being heated to 750 DEG C with the heating rate of 100 DEG C/s, heat preservation 7s is carried out
Inverse austenitizing is handled, and is then quenched to room temperature with the rate of temperature fall of 100 DEG C/s.
5) 500 DEG C will be heated to the heating rate of 100 DEG C/s, and keep the temperature 60s carry out tempering, then with 100 DEG C/
The rate of temperature fall fast cooling of s is to room temperature.Embodiment 4
High-strength and high ductility processing is carried out for certain model Steel material, the chemical component of the Steel material are as follows: Mn:3.69%, C:
0.39%, P:0.009%, S:0.0034%, N:0.0026%, Si:0.01%, remaining is iron and inevitable impurity member
Element, it is 720 DEG C that ferrite, which is completely converted into the finishing temperature of austenite, in the Steel material, the route map for the treatment of process such as Fig. 1
Shown, specific processing step is as follows:
1) melted steel material is subjected to three piers three and pulls out forging technology, the specific steps are as follows:
Process 1: initial forging temperature is 1150 DEG C, the half of upsetting to height, then is pulled out to former height；
Process 2: melting down heating temperature is 1080 DEG C, the half of upsetting to height, then is pulled out to former height；
Process 3: melting down heating temperature is 1050 DEG C, the half of upsetting to height；
Process 4: it is forged again to the square billet with a thickness of 20mm；The final forging temperature of above-mentioned operation is 820 DEG C.
2) pearliteization is handled: steel material is heated to 840 DEG C and is kept the temperature 5min carry out with the heating rate of 30 DEG C/s
Then complete austenitizing is cooled at 575 DEG C of medium temperature of perlitic transformation temperature range with the rate of temperature fall of 30 DEG C/s
It keeps the temperature 4h and carries out complete pearlite, room temperature is then down to the rate of temperature fall of 30 DEG C/s.
3) inverse austenitizing is handled: and then, steel material being heated to 750 DEG C with the heating rate of 30 DEG C/s, heat preservation
40s carries out inverse austenitizing and handles, and is then quenched with rate of temperature fall fast cooling to the room temperature of 100 DEG C/s.
4) tempering: and then 400 DEG C will be heated to the heating rate of 30 DEG C/s, and keep the temperature 60s and carries out at tempering
Reason, then with the rate of temperature fall fast cooling of 100 DEG C/s to room temperature.
Test 1: the sample after handling (750 DEG C of -7s) against austenitizing to 1 step 4 of embodiment carries out XRD test, obtains
Diffraction pattern as shown in Fig. 2, as seen from the figure, sample mainly has γ ((200), (220)) and α ' after inverse austenitizing processing
((200), (211)) two-phase, wherein γ is retained austenite, and α ' is martensite.
Test 2: XRD test is carried out to the sample after the different tempering temperature temperings of Examples 1 to 3 step 5 respectively, is obtained
The diffraction pattern arrived is as shown in figure 3, the sample after same tempering is also mainly γ and α ' two-phase.
Test 3: SEM observation is carried out against austenitizing treated sample to step 4 in embodiment 1, obtains microstructure
Figure, as shown in Figure 4；SEM observation is carried out to the sample after step 5 tempering in embodiment 1, obtains micro-organization chart, such as Fig. 5
It is shown；As seen from Figure 4, discovery most tissues are in lamellar in sample after inverse austenitizing processing, can be seen by Fig. 5
Out, most of tissue of sample after tempering is in lamellar.
Test 4: tem observation is carried out against austenitizing treated sample to step 4 in embodiment 1, obtains light field phasor
As shown in fig. 6, to obtain dark field phase images as shown in Figure 7；Tem observation is carried out to the sample after 2 tempering of embodiment, is obtained
Light field phase images as shown in figure 8, obtain dark field phase images as shown in figure 9, demarcating by the diffraction spot to lamellar microstructure,
As a result it is FCC and BCC two-phase, in conjunction with XRD diffraction patterns, by Fig. 6, Fig. 7, Fig. 8, Fig. 9, can significantly sees that sheet remains
The overlapping tissue of austenite and synusia martensite.
Test 5: to the finally obtained Steel material of Examples 1 to 4 according to following testing standard (GB/T 228.1-2010) point
Not carry out room temperature tensile Mechanics Performance Testing, obtain tensile stress strain curve as shown in Figure 10.It can be seen that from the curve
For Steel material after the inverse austenitizing-tempering process of pearlite-, yield strength can reach 1.5GPa or more, resist
Tensile strength can reach 1.8GPa or more, and elongation percentage can reach 10% or more.
It is the explanation of preferred embodiment for the present invention above.Here, it should be noted is that, the present invention not office
It is limited to above embodiments, it, can be to this hair in the case where meeting the area requirements such as claims, summary of the invention and attached drawing
Any modification, same replacement made by bright or improvement etc., should be included within the scope of the present invention.
Claims (7)
1. it is a kind of obtain the advanced high-strength steel of high-strength and high ductility treatment process, it is characterized in that the treatment process the following steps are included:
1) pearliteization is handled: Steel material is heated to Ae3On 10 DEG C~300 DEG C of austenitizing temperature, and in above-mentioned Ovshinsky
1min~120min is kept the temperature at a temperature of body, will be down to perlitic transformation temperature range by the Steel material of austenitizing: 470 DEG C
~700 DEG C, heat preservation 0.1h~6h obtains complete pearlitic structrure, then cools to room temperature, wherein Ae3For in the Steel material
Ferrite is completely converted into the finishing temperature of austenite；
2) inverse austenitizing is handled: will be again heated to Ae by the Steel material of pearliteization processing3On 1 DEG C~50 DEG C, heat preservation
1s~300s makes the Steel material carry out the inverse austenitizing changed from processing from pearlite to austenite, is then quenched to room temperature；
3) tempering: will be by inverse austenitizing treated Steel material with the heating of 30 DEG C/s~100 DEG C/s heating rate
To 150 DEG C~500 DEG C of tempering temperature, room temperature is down to 50 DEG C/s~200 DEG C/s rate of temperature fall after heat preservation 10s~300s；
The treatment process is suitable for inclusion in the Steel material of carbon and manganese element.
2. a kind for the treatment of process for obtaining the advanced high-strength steel of high-strength and high ductility as described in claim 1, it is characterized in that: in the 1) step
Before carrying out pearlite, Homogenization Treatments first are carried out to Steel material.
3. a kind for the treatment of process for obtaining the advanced high-strength steel of high-strength and high ductility as described in claim 1, it is characterized in that: in the 1) step
Before carrying out pearlite, first Steel material is rolled or forged.
4. a kind for the treatment of process of advanced high-strength steel of acquisition high-strength and high ductility as described in any one of claim 1-3, special
Sign is: the heating rate of heating is 30 DEG C/s~100 DEG C/s when carrying out austenitizing in the 1) step.
5. a kind for the treatment of process of advanced high-strength steel of acquisition high-strength and high ductility as described in any one of claim 1-3, special
Sign is: the Steel material in the 1) step by austenitizing be down to perlitic transformation temperature range rate of temperature fall be 10 DEG C/s~
50℃/s。
6. a kind for the treatment of process of advanced high-strength steel of acquisition high-strength and high ductility as described in any one of claim 1-3, special
Sign is: by the rate of temperature fall for being down to room temperature by the Steel material of complete pearlite being 30 DEG C/s~100 DEG C/s in the 1) step.
7. a kind for the treatment of process of advanced high-strength steel of acquisition high-strength and high ductility as described in any one of claim 1-3, special
Sign is: the heating rate heated when carrying out inverse austenitizing in the 2) step is 30 DEG C/s~100 DEG C/s；It is quenched to the drop of room temperature
Warm rate is 50 DEG C/s~200 DEG C/s.
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Cited By (6)
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| CN112251679A (en) * | 2020-09-18 | 2021-01-22 | 东南大学 | Double-phase high-strength steel and preparation method thereof |
| CN112342345A (en) * | 2020-09-28 | 2021-02-09 | 东南大学 | Martensite/austenite dual-phase structure high-strength steel and preparation method thereof |
| CN113061698A (en) * | 2021-03-16 | 2021-07-02 | 北京理工大学 | Heat treatment method for preparing quenching-partitioning steel by taking pearlite as precursor |
| CN113652612A (en) * | 2021-08-19 | 2021-11-16 | 北京理工大学 | Manganese steel in heterogeneous lamellar structure and preparation method thereof |
| CN116144887A (en) * | 2022-09-09 | 2023-05-23 | 北京理工大学 | Quenching-distribution heat treatment method for realizing silicon-free and aluminum-free medium manganese steel |
| CN116949366A (en) * | 2023-08-01 | 2023-10-27 | 北京理工大学 | Carbide-free tempered martensitic steel and method for producing same |
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