CN109439853A - Novel low-alloy super-strength steel and thermomechanical treatment process - Google Patents
Novel low-alloy super-strength steel and thermomechanical treatment process Download PDFInfo
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- CN109439853A CN109439853A CN201811294689.8A CN201811294689A CN109439853A CN 109439853 A CN109439853 A CN 109439853A CN 201811294689 A CN201811294689 A CN 201811294689A CN 109439853 A CN109439853 A CN 109439853A
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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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
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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
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/005—Modifying the physical properties by deformation combined with, or followed by, heat treatment of ferrous alloys
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
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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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/008—Martensite
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- Heat Treatment Of Steel (AREA)
Abstract
The invention belongs to alloy fields, and in particular to a kind of novel low-alloy super-strength steel and thermomechanical treatment process.Novel low-alloy super-strength steel includes following content of component: C 0.23-0.27%, Si 0.17-0.35%, Mn 0.35-0.6%, Cr 0.95-1.1%, Mo 0.70-0.90%, Nb 0.01-0.04%, V 0.08-0.12%, Ti 0.01-0.04%, remaining is Fe and impurity.Certain ingredient design and processes are carried out to low-alloy super-strength steel by early period to adjust, it only need to controlled strain rate be simply that can promote the precipitation of MX phase in low-alloy super-strength steel in subsequent deformation heat treatment process, martensite lath width can be also refined simultaneously, simple process, purpose is strong, is of great significance to the toughness and tenacity for improving low-alloy super-strength steel.
Description
Technical field
The invention belongs to alloy fields, and in particular to a kind of novel low-alloy super-strength steel and thermomechanical treatment process.
Background technique
With the continuous development of the every field such as aerospace, high-speed railway, deep-ocean resource exploitation, automotive light weight technology, make
For the primary structure steel in these fields, low-alloy super-strength steel need to be on active service in the environment of awful weather, complicated geology, hold
By the multiple test such as higher external and internal pressure, axial tensile loads, low temperature and corrosion.It is special to the comprehensive performance of unimach
It is not that obdurability proposes harsh requirement.Currently, the low-alloy super-strength steel performance indexes of China's autonomous production is still not
Stablize, therefore, the research and development for accelerating independent brand low-alloy super-strength steel is needed, to promote the production domesticization of unimach to provide
Scientific basis.
The key of low-alloy super-strength steel production domesticization is to improve the toughness and tenacity of material.The raising of intensity is inevitable
The hardness for increasing material, cause unimach notch sensitivity to increase, be easy to generate stress corrosion cracking and influence material
Expect the service life.Studies have shown that: strictly being controlled by pure smelting to the chemical component uniformity and degree of purity of unimach
System, can effectively improve the toughness of steel.The addition of alloying element also can tissue to unimach and obdurability generate shadow
It rings, by the rational proportion of alloying element, reduces the Ms point of unimach, make to be quenched to retained austenite in the tissue of room temperature
Content increases, and effectively improves the modeling of material, tough performance.In conjunction with thermomechanical treatment mode appropriate, microalloy atom is in steel
It can be combined with C or N atom.The different precipitate of these types, form, size is by crystal grain refinement, precipitation strength, and two
The effects of underhardening, strengthens matrix, and material is made to obtain the intensity and good plastic toughness of superelevation.Currently, passing through accurate deformation
Heat treatment process realizes that effective control of compound low-alloy super-strength steel tissue and precipitate is not yet reported in media.
Summary of the invention
It is an object of the invention to overcome the deficiencies of existing technologies, a kind of novel low-alloy super-strength steel and deformation are provided
Heat treatment process.
The present invention to achieve the above object, using following technical scheme:
A kind of novel low-alloy super-strength steel, including following content of component: C 0.23-0.27%, Si 0.17-
0.35%, Mn 0.35-0.6%, Cr 0.95-1.1%, Mo 0.70-0.90%, Nb 0.01-0.04%, V 0.08-
0.12%, Ti 0.01-0.04%, remaining is Fe and impurity.
Preferably, including following mass components: C 0.25%, Si 0.29%, Mn 0.39%, Cr 0.97%, Mo
0.85%, Nb 0.012%, V 0.089%, Ti 0.026%, impurity are P 0.005%, S 0.001%, remaining is Fe.
The application further includes the thermomechanical treatment process of novel low-alloy super-strength steel described in one kind, including following steps
It is rapid: 1200-1300 DEG C of heat preservation 5-30min being heated to 10-20 DEG C/s and is then cooled to respectively with the cooling velocity of 20-30 DEG C/s
900-1200 DEG C, be 0.01-10s respectively with strain rate-1, compressive deformation is carried out, deflection 60% is direct after the completion of deformation
Water cooling is to room temperature.
Compared with prior art, the beneficial effects of the present invention are:
The present invention is compound in novel low-alloy super-strength steel to be added to the microalloy elements such as Nb, V, Ti, microalloy member
Element main forms in unimach are dissolved into matrix for microalloy element plays the role of solution strengthening；With C, N
The effects of atom combines, and forms carbon, nitride second phase particles, plays precipitation strength, refined crystalline strengthening.In order to give full play to
Secondary phase particle improves the effect of unimach toughness and tenacity, by accurate thermomechanical treatment process, promote thermal stability compared with
High MX phase is precipitated.Obtain using compared with hardenite as matrix, and on matrix the tiny MX phase of Dispersed precipitate tissue, can improve
The toughness and tenacity of material.Use the present invention at 1200 DEG C with differently strained rate (0.01s-1、10s-1) martensite lath after deformation
Width significantly refines, and martensite lath width is respectively 178.45nm, 87.60nm in sample.Strain rate raising can promote two
The different MX phase of kind chemical component, form, size is precipitated, and size is gradually reduced.Strain rate is 0.01s-1And 10s-1
Under the conditions of, the MX phase size of rectangular richness Ti is down to 58.74nm by 70.52nm, and the MX phase size of spherical richness Nb is down to by 8.67nm
5.34nm.The present invention is precipitated by two kinds of MX phases of thermomechanical treatment process promotion and size is gradually reduced.MX phase is with higher
Thermodynamic stability still is able to effective pinning crystal boundary under higher austenitizing temperature, plays the role of refining crystal grain,
Further increase the toughness and tenacity of low-alloy super-strength steel.Compared with traditional heat treatment process, thermomechanical treatment process letter
Change process flow, reduced production cost, improves comprehensive performance, therefore present invention could apply in actual production.It is logical
It spends early period and carries out certain ingredient design and processes adjustment to low-alloy super-strength steel, in subsequent deformation heat treatment process only
It need to controlled strain rate be simply that can promote the precipitation of MX phase in low-alloy super-strength steel, while can also refine martensite plate
Width, simple process, purpose is strong, is of great significance to the toughness and tenacity for improving low-alloy super-strength steel.
Detailed description of the invention
Fig. 1 (a) is transmission electron microscope (TEM) photo of low-alloy super-strength steel martensite lath in embodiment 1；
Fig. 1 (b) is MX phase transmission electron microscope (TEM) photo of richness Ti in low-alloy super-strength steel in embodiment 1；
Fig. 1 (c) is MX phase transmission electron microscope (TEM) photo of richness Nb in low-alloy super-strength steel in embodiment 1；
Fig. 2 (a) is transmission electron microscope (TEM) photo of low-alloy super-strength steel martensite lath in embodiment 2；
Fig. 2 (b) is MX phase transmission electron microscope (TEM) photo of richness Ti in low-alloy super-strength steel in embodiment 2；
Fig. 2 (c) is MX phase transmission electron microscope (TEM) photo of richness Nb in low-alloy super-strength steel in embodiment 2.
Specific embodiment
In order to make those skilled in the art more fully understand technical solution of the present invention, with reference to the accompanying drawing and most
The present invention is described in further detail for good embodiment.
Embodiment 1: low-alloy super-strength steel of the present invention is made of the following components according to mass percent than tool: C
0.25%, Si 0.29%, Mn 0.39%, Cr 0.97%, Mo 0.85%, Nb 0.012%, V 0.089%, Ti
0.026%, impurity is P 0.005%, S 0.001%, remaining is Fe.
Martensite lath refinement and promotion MX phase separation method to the novel low-alloy super-strength steel of the present invention, deformation
The step of heat treatment process, is: the unimach being processed into the cylindrical specimens of 8 × 10mm of Φ, in Gleeble-1500 heat
Thermomechanical treatment process experiment is carried out on simulation test machine.1250 DEG C of abundant austenitizings of heat preservation 10min are warming up to 10 DEG C/s,
It is cooled to 1200 DEG C with the cooling velocity of 30 DEG C/s, with strain rate 0.01s-1, carry out compressive deformation, deflection 60%, deformation
Direct water-cooling is to room temperature after the completion.
Fig. 1 (a) is transmission electron microscope (TEM) photo of low-alloy super-strength steel martensite lath in embodiment 1, after measured
Use the present invention at 1200 DEG C with 0.01s-1Martensite lath width is about 178.45nm after strain rate deformation.Fig. 1 (b) is real
Apply MX phase transmission electron microscope (TEM) photo of richness Ti in low-alloy super-strength steel in example 1, it can be seen that strain rate 0.01s-1
Under the conditions of, the MX phase of rich Ti is rectangular or rectangle, and average-size is about 70.52nm.Fig. 1 (c) is low-alloy superelevation in embodiment 1
MX phase transmission electron microscope (TEM) photo of richness Nb in strength steel, it can be seen that strain rate 0.01s-1Under the conditions of, the MX phase of rich Nb
To be spherical, average-size is about 8.67nm.
Embodiment 2:
Low-alloy super-strength steel of the present invention is made of the following components according to mass percent than tool: C 0.25%, Si
0.29%, Mn 0.39%, Cr 0.97%, Mo 0.85%, Nb 0.012%, V 0.089%, Ti 0.026%, impurity P
0.005%, S 0.001%, remaining is Fe.
Martensite lath refinement and promotion MX phase separation method to the novel low-alloy super-strength steel of the present invention, deformation
The step of heat treatment process, is: the unimach being processed into the cylindrical specimens of 8 × 10mm of Φ, in Gleeble-1500 heat
Thermomechanical treatment process experiment is carried out on simulation test machine.1250 DEG C of abundant austenitizings of heat preservation 10min are warming up to 10 DEG C/s,
It is cooled to 1200 DEG C with the cooling velocity of 30 DEG C/s, with strain rate 10s-1, compressive deformation is carried out, deflection 60% has deformed
At rear direct water-cooling to room temperature.
Fig. 2 (a) is transmission electron microscope (TEM) photo of low-alloy super-strength steel martensite lath in embodiment 2, can be seen
Out, strain rate increases significant refinement martensite lath, uses the present invention at 1200 DEG C with 10s after measured-1Strain rate deformation
Martensite lath width is about 87.60nm afterwards.The MX phase that Fig. 2 (b) is richness Ti in low-alloy super-strength steel in embodiment 2 transmits
Electronic Speculum (TEM) photo, it can be seen that strain rate 10s-1Under the conditions of, the MX phase size of rich Ti is 0.01s compared with strain rate-1
When refinement it is obvious, average-size is about 58.74nm.The MX phase that Fig. 2 (c) is richness Nb in low-alloy super-strength steel in embodiment 2
Transmission electron microscope (TEM) photo, it can be seen that strain rate increase effectively facilitates the precipitation of the MX phase of rich Nb, and size more refinement
It is small, it is 10s through measurement strain rate-1Under the conditions of, the MX phase average size of rich Nb is about 5.34nm.
Embodiment 3: low-alloy super-strength steel of the present invention is made of the following components according to mass percent than tool: C
0.23%, Si 0.17%, Mn 0.35%, Cr 0.95%, Mo 0.70%, Nb 0.01%, V 0.08%, Ti 0.01%,
Impurity is P 0.005%, S 0.001%, remaining is Fe.
Martensite lath refinement and promotion MX phase separation method to the novel low-alloy super-strength steel of the present invention, deformation
The step of heat treatment process, is: the unimach being processed into the cylindrical specimens of 8 × 10mm of Φ, in Gleeble-1500 heat
Thermomechanical treatment process experiment is carried out on simulation test machine.1200 DEG C of abundant austenitizings of heat preservation 30min are warming up to 20 DEG C/s,
It is cooled to 900 DEG C with the cooling velocity of 20 DEG C/s, with strain rate 0.05s-1, compressive deformation is carried out, deflection 60% has deformed
At rear direct water-cooling to room temperature.
Embodiment 4: embodiment 1: low-alloy super-strength steel of the present invention has following components group according to mass percent ratio
At: C 0.27%, Si 0.35%, Mn 0.6%, Cr 1.1%, Mo 0.9%, Nb 0.04%, V 0.12%, Ti
0.04%, impurity is P 0.005%, S 0.001%, remaining is Fe.
Martensite lath refinement and promotion MX phase separation method to the novel low-alloy super-strength steel of the present invention, deformation
The step of heat treatment process, is: the unimach being processed into the cylindrical specimens of 8 × 10mm of Φ, in Gleeble-1500 heat
Thermomechanical treatment process experiment is carried out on simulation test machine.1250 DEG C of abundant austenitizings of heat preservation 10min are warming up to 15 DEG C/s,
It is cooled to 1200 DEG C with the cooling velocity of 25 DEG C/s, with strain rate 10s-1, compressive deformation is carried out, deflection 60% has deformed
At rear direct water-cooling to room temperature.
Although above in conjunction with figure, invention has been described, and the invention is not limited to above-mentioned specific embodiment parties
Formula, the above mentioned embodiment is only schematical, rather than restrictive, and those skilled in the art are in this hair
Under bright enlightenment, without deviating from the spirit of the invention, many variations can also be made, these belong to guarantor of the invention
Within shield.
Claims (3)
1. a kind of novel low-alloy super-strength steel, which is characterized in that including following content of component: C 0.23-0.27%, Si
0.17-0.35%, Mn 0.35-0.6%, Cr 0.95-1.1%, Mo 0.70-0.90%, Nb 0.01-0.04%, V 0.08-
0.12%, Ti 0.01-0.04%, remaining is Fe and impurity.
2. novel low-alloy super-strength steel according to claim 1, it is characterised in that: including following content of component: C
0.25%, Si 0.29%, Mn 0.39%, Cr 0.97%, Mo 0.85%, Nb 0.012%, V 0.089%, Ti
0.026%, impurity is P 0.005%, S 0.001%, remaining is Fe.
3. a kind of thermomechanical treatment process of the described in any item novel low-alloy super-strength steels of claim 1-2, feature
It is, includes the following steps: to be heated to 1200-1300 DEG C of heat preservation 5-30min with 10-20 DEG C/s, then, with 20-30 DEG C/s's
Cooling velocity is cooled to 900-1200 DEG C respectively, is 0.01-10s respectively with strain rate-1, compressive deformation is carried out, deflection is
60%, direct water-cooling is to room temperature after the completion of deformation.
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Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US6767416B2 (en) * | 2001-02-27 | 2004-07-27 | Hitachi, Ltd. | Corrosion resistant, high strength alloy and a method for manufacturing the same |
| UA79726C2 (en) * | 2006-12-04 | 2007-07-10 | Nat Scient Ct Kharkiv Physical | Method for treatment of stainless steel of austenitic grade |
| CN102703837A (en) * | 2012-05-25 | 2012-10-03 | 燕山大学 | Nano-structured lath martensite steel and preparation method thereof |
| CN107257865A (en) * | 2015-02-06 | 2017-10-17 | 艾森曼欧洲公司 | For carrying out deformation heat treatment method, furnace apparatus and system to workpiece |
| CN108624810A (en) * | 2017-06-26 | 2018-10-09 | 宝山钢铁股份有限公司 | A kind of high sulfur resistive oil well pipe of low-cost high-strength and its manufacturing method |
-
2018
- 2018-11-01 CN CN201811294689.8A patent/CN109439853A/en active Pending
Patent Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US6767416B2 (en) * | 2001-02-27 | 2004-07-27 | Hitachi, Ltd. | Corrosion resistant, high strength alloy and a method for manufacturing the same |
| UA79726C2 (en) * | 2006-12-04 | 2007-07-10 | Nat Scient Ct Kharkiv Physical | Method for treatment of stainless steel of austenitic grade |
| CN102703837A (en) * | 2012-05-25 | 2012-10-03 | 燕山大学 | Nano-structured lath martensite steel and preparation method thereof |
| CN107257865A (en) * | 2015-02-06 | 2017-10-17 | 艾森曼欧洲公司 | For carrying out deformation heat treatment method, furnace apparatus and system to workpiece |
| CN108624810A (en) * | 2017-06-26 | 2018-10-09 | 宝山钢铁股份有限公司 | A kind of high sulfur resistive oil well pipe of low-cost high-strength and its manufacturing method |
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