CN102127711A - Nano-structured ultrahigh-strength dual-phase steel and production method thereof - Google Patents
Nano-structured ultrahigh-strength dual-phase steel and production method thereof Download PDFInfo
- Publication number
- CN102127711A CN102127711A CN 201110042031 CN201110042031A CN102127711A CN 102127711 A CN102127711 A CN 102127711A CN 201110042031 CN201110042031 CN 201110042031 CN 201110042031 A CN201110042031 A CN 201110042031A CN 102127711 A CN102127711 A CN 102127711A
- Authority
- CN
- China
- Prior art keywords
- steel
- nanostructure
- superstrength
- production method
- dual phase
- 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.)
- Granted
Links
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
- C21D1/18—Hardening; Quenching with or without subsequent tempering
- C21D1/25—Hardening, combined with annealing between 300 degrees Celsius and 600 degrees Celsius, i.e. heat refining ("Vergüten")
-
- 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
- C21D1/44—Methods of heating in heat-treatment baths
- C21D1/46—Salt baths
-
- 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
- C21D1/56—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering characterised by the quenching agents
- C21D1/60—Aqueous agents
-
- 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
- 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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/008—Heat treatment of ferrous alloys containing Si
-
- 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
-
- 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
-
- 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
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
-
- 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
-
- 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
-
- 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
-
- 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
-
- 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
- C22C38/34—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of silicon
-
- 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
- C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
-
- 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
- C21D2211/001—Austenite
-
- 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
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Heat Treatment Of Steel (AREA)
Abstract
The invention relates to nano-structured ultrahigh-strength dual-phase steel and a production method thereof. The production method comprises the following steps: austenitizing steel billet at 850-1,050 DEG C for 0.2-0.6 hour; water-bath quenching at 0-100 DEG C, and holding the temperature for 1.0-10.0 minutes; performing carbon distribution and tempering at 300-600 DEG C for 0.01-1.0 hour; and fnally quenching with water to room temperature. The medium for carbon distribution and tempering is one of salt bath, inert gas atmosphere and weak reducing atmosphere. The steel billet comprises the following chemical components in percentage by weight: C 0.71-1.00, Si 1.00-2.00, Mn 1.00-2.00, Cr 1.00-1.60, Mo 0.05-1.00, Al 0.05-1.00, Nb 0.00-0.2, Ti 0.00-0.2%, V 0.00-0.2%, P less than 0.015%, S less than 0.010%, and Fe and unavoidable impurities as balance, wherein the sum of the contents of Si, Mn, Cr, Mo and Al is less than or equal to 6.00%, and the sum of the contents of Nb, Ti and V is less than or equal to 0.30%. The production method provided by the invention has the characteristics of low cost, simple process and short heat treatment cycle; and the produced steel plate has good properties and wide application range.
Description
Technical field
The invention belongs to the ultrahigh-strength steel technical field.Be specifically related to a kind of superstrength dual phase steel and manufacture method thereof of nanostructure.
Background technology
It has been generally acknowledged that tensile strength surpasses 1500N/mm
2Structural alloy steel be ultrahigh-strength steel.Ultrahigh-strength steel is to grow up on the basis of structural alloy steel, by special alloying constituent and Design of Heat Treatment Process, reached the intensity rank of superelevation, be mainly used in and make undercarriage and girder, solid rocket motor case, supercentrifuge rotary barrel and other bear heavily stressed structure unit.Traditional ultrahigh-strength steel according to chemical composition is divided into highly malleablized mechanism usually:
(1) low-alloy super-strength steel grows up on the quenching and tempering steel basis, its w
C=0.30%～0.45%, w
MeAbout=5%.The normal alloying element that adds has Ni, Cr, Mo, V, Ti, Nb, Al, Si, Mn etc., and its effect is hardening capacity, solution strengthening, crystal grain thinning and raising tempered martensite and the ferritic stability that improves steel.By quenching and tempering or means of isothermal quenching, can obtain the mixed structure of tempered martensite or lower bainite+tempered martensite.Though this class steel has higher intensity and certain plasticity, owing to wherein do not contain retained austenite, its plasticity is much smaller than TRIP steel (transformation induced plasticity steel) and DP steel (dual phase steel).
(2) secondary hardening type ultrahigh-strength steel means by behind the quenching+high tempering, separates out the specific alloy carbide and reaches the ultrahigh-strength steel of dispersion-strengthened (secondary hardening) effect.Mainly comprise carbon interalloy martensite hot-work die steel in the Cr-Mo-V type, high tenacity 9Ni-4Co type and 10Ni-14Co type high-ductility ultrahigh-strength steel.This class steel contains very high alloying elements such as noble metal Ni, Co, cost of alloy costliness.
(3) maraging steel, i.e. 18Ni Mo ultralow-carbon martensitic aging steel.It is Fe-Ni based Ultra-low carbon High-alloy Ultra-high Strength Steel.Reach the ultrahigh-strength steel of strengthening effect by compound between martensitic transformation and timeliness precipitating metal.This class steel generally adopts vacuum induction melting to add two vacuum metling technologies of consumable electrode vacuum furnace remelting, this complex process, and contain very high alloy, alloy and production cost costlinesses such as noble metal Ni, Mo in the steel.
(4) superhigh strength stainless steel, it grows up on stainless steel base, has higher intensity and solidity to corrosion.Different according to its tissue and strengthening mechanism also can be divided into martensitic precipitation, semiaustenitic PH Stainless Steel and martensite aged stainless steel etc.This class steel contains alloys such as very high Ni, Cr, so its price is also very expensive.
The bainitic steel of nanostructure because its microstructure is the nanometer ferrite bainite, adds to have a large amount of retained austenites, has the intensity of superelevation, good plasticity and good impelling strength, its excellent comprehensive mechanical property.Through existing literature and patent retrieval are found, the F.G.Caballero of univ cambridge uk, people such as H.K.D.B.Bhadeshia are at " Very Strong Bainite; Current Opinion in Solid and Materials Science; 8 (2004): p.251-257. ", " Carbon supersaturation of ferrite in a nanocrystalline bainitic steel; Acta Materialia; 58 (2010): p.2338-2343. " etc. set forth the preparation technology of nanometer bainitic steel in the article, obtained superstrength nanostructure bainitic steel.High-carbon, high silicon steel carry out long-time isothermal transformation at low temperature (200～300 ℃) and can obtain superfine little bainite structure, have superstrength and excellent toughness, applied for multinomial patent, such as " METHOD FOR PRODUCING AN IMPROVEDBAINITIC STEEL " (EP 1200638 (A1)), " A steel and a heat treatment for steels " (GB2352726 (A)), " HIGH STRENGTH BAINITIC STEEL FOR OCTG APPLICATIONS " patented technologies such as (WO2009065432 (A1)).But its shortcoming be heat treatment time long (several days even longer), even the Elements C o that increases γ → α free energy with (or) Al, also need time a couple of days, the thermal cycle is long.
The J.G.Speer of Colorade USA mining industry university, people such as D.V.Edmonds are at " Carbon partitioning into austenite after martensite transformation; Acta Materialia; 51 (2003): p.2611-2622. ", " Partitioning of carbon from supersaturated plates of ferrite.with application to steel processing and fundamentals of the bainite transformation; Current Opinion in Solid and Materials Science; 8 (2004): p.219-237. " etc. set forth the novel thermal process technology that quenching-carbon distributes (Q-P) in the article, obtain superstrength martensite-retained austenite steel, be quenched into certain temperature, and then carry out the carbon allocation process, utilize the distribution principle of carbon atom from martensite to the retained austenite, can make the rich carbon of retained austenite, and then at room temperature obtain stable retained austenite, have superstrength and excellent toughness.But its shortcoming is not add strong carbide to separate out element, does not introduce the precipitation strength of carbide.
People such as the Zhong Ning of Chinese Shanghai university of communications, Xu Zuyao are at " high strength Q﹠amp; The research of P steel and Q-P-T steel, Shanghai Communications University's Ph D dissertation, 2009. "; " the heat treated novel process of steel, thermal treatment, 22 (2007): the thermal treatment process of p.1-11. " etc. having set forth quenching-carbon distribution-tempering (Q-P-T) in the article; obtain superstrength nanostructure martensitic steel; low-carbon (LC) and medium carbon alloy steel are through Q-P-T thermal treatment; because the precipitation strength effect of carbide; than Q-P steel higher intensity is arranged; have the intensity of superelevation, keep good plasticity and toughness simultaneously, applied for multinomial patent, such as " adopting carbon to distribute the method that improves steel object surface hardness " (200610029690), " distribution of employing carbon and tempering improve the heat treating method of quenched steel component mechanical property " patented technologies such as (200710045886).But its shortcoming is will carry out repeatedly the salt bath medium heat to handle the technology relative complex; And the volume fraction of resulting retained austenite is generally all less than 10%, and is limited to the raising of toughness and plasticity.
Summary of the invention
The present invention is intended to overcome above-mentioned technological deficiency, purpose provide a kind of with low cost, technology is simple, heat treatment cycle is short, the superstrength nanostructure dual phase steel and the manufacture method thereof of excellent property.
For achieving the above object, the technical solution used in the present invention is: earlier with steel billet austenitizing 0.2～0.6 hour under 850～1050 ℃ of conditions; Under 0～100 ℃ of condition, carry out water-bath again and quench, be incubated 1.0～10.0 minutes; Carry out carbon distribution+tempering then under 300～600 ℃ of conditions, the time is 0.01～1.0 hour; Last shrend is to room temperature.
Carbon distribution+tempered medium is a kind of in salt bath, inert atmosphere and the faint reducing atmosphere.
The chemical ingredients and the content thereof of steel billet are: C is 0.71～1.00wt%, Si is 1.00～2.00wt%, and Mn is 1.00～2.00wt%, and Cr is 1.00～1.60wt%, Mo is 0.05～1.00wt%, Al is 0.05～1.00wt%, and Nb is 0.00～0.2wt%, and Ti is 0.00～0.2wt%, V is 0.00～0.2wt%, P＜0.015wt%, S＜0.010wt%, all the other are Fe and unavoidable impurities; Wherein, Si+Mn+Cr+Mo+Al≤6.00wt%, Nb+Ti+V≤0.30wt%.
Because adopt technique scheme, the present invention is based on cheap C, Si, Mn, Cr element, has only elements such as a spot of Mo, Al, Nb, V, Ti, so with low cost; Quench with water-bath, carry out carbon distribution+tempered thermal treatment process afterwards under the condition of inert atmosphere or faint reducing atmosphere or salt bath, so thermal treatment process is simple, whole heat treatment process only needs 0.3～1.7 hour, and heat treatment cycle is short.
The microstructure of the superstrength nanostructure dual phase steel of manufacturing of the present invention is that the martensite lath of nano level (～100nm thickness) is a matrix, the distributing super fine organization of carbide of retained austenite and nano-scale (～10nm diameter) of disperse.The volume fraction of retained austenite accounts for bigger ratio (10～40vol%).The lath martensite tissue of nanostructure, toughness and breaking resistance with superelevation; Austenite is the toughness phase, be distributed on the martensite lath or between the lath, be subjected under the external force effect viscous deformation taking place, absorb and consumed energy, delay the expansion of crackle, extremely beneficial to the toughness that improves sheet material, stress can undergo phase transition induced plasticity effect (TRIP effect) when big, further improves the toughness of steel; The carbide of nano-scale further increases its intensity.Because of the solution strengthening of carbon, dislocations strengthening, martensite lath are strengthened, induced plasticity is strengthened, the precipitation strength of carbide etc., make this steel can reach the intensity rank of superelevation; Distribute because of retained austenite becomes fine strip shape, and volume content is bigger, makes this steel reach good plasticity rank, its comprehensive mechanical property excellence.
The tensile strength of the superstrength nanostructure dual phase steel of manufacturing of the present invention is that 1800～2550MPa, hardness are that 550～700HV, unit elongation are 15～30%, fracture toughness is 20～35MPam
1/2The superstrength nanostructure dual phase steel of manufacturing is with respect to the nanostructure bainitic steel, and not only its heat treatment time shortens greatly, and its intensity, hardness, plasticity, toughness is higher than or be equivalent to the nanostructure bainitic steel; With respect to the nanostructure martensitic steel of low-carbon (LC) and middle carbon, its intensity and hardness significantly improve, and plasticity and toughness also are higher than other steel grades of analogous components.
Therefore, the characteristics that the present invention has is with low cost, technology is simple and heat treatment cycle is short, prepared plate property is good, can be widely used in making undercarriage and girder, solid rocket motor case, supercentrifuge rotary barrel and other bear heavily stressed structure unit.
Embodiment
Below in conjunction with embodiment the present invention being further described, is not limiting the scope of the invention.
Embodiment 1
A kind of superstrength dual phase steel and manufacture method thereof of nanostructure.Earlier with steel billet austenitizing 0.2～0.5 hour under 900～1050 ℃ of conditions; Under the condition of 50～100 ℃ of water-baths, quench then, be incubated 4.0～10.0 minutes; Carry out carbon distribution+tempering afterwards under 300～500 ℃ inert atmosphere conditions, the time is 0.4～1.0 hour; Last shrend is to room temperature.
The chemical ingredients and the content thereof of steel billet are: C is 0.71～0.90wt%, Si is 1.00～1.50wt%, and Mn is 1.50～2.00wt%, and Cr is 1.00～1.60wt%, Mo is 0.05～0.60wt%, Al is 0.05～0.60wt%, and Nb is 0.05～0.2wt%, and Ti is 0.05～0.2wt%, V is 0.05～0.2wt%, P＜0.015wt%, S＜0.010wt%, all the other are Fe and unavoidable impurities; Wherein, Si+Mn+Cr+Mo+Al≤6.00wt%, Nb+Ti+V≤0.30wt%.
The tensile strength of the superstrength nanostructure dual phase steel of present embodiment manufacturing is 1800～2300MPa, and hardness is 550～640HV, and unit elongation is 20～30%, and fracture toughness is 25～35MPam
1/2Superstrength nanostructure dual phase steel.
Embodiment 2
A kind of superstrength dual phase steel and manufacture method thereof of nanostructure.Earlier with steel billet austenitizing 0.25～0.55 hour under 870～1020 ℃ of conditions; Under the condition of 20～80 ℃ of water-baths, quench then, be incubated 3.0～9.0 minutes; Carry out carbon distribution+tempering afterwards under the condition of 350～600 ℃ faint reducing atmosphere, the time is 0.2～0.7 hour; Last shrend is to room temperature.
The chemical ingredients and the content thereof of steel billet are: C is 0.75～0.95wt%, Si is 1.50～2.00wt%, Mn is 1.00～1.50wt%, and Cr is 1.00～1.60wt%, and Mo is 0.40～1.00wt%, Al is 0.40～1.00wt%, Nb is 0.05～0.2wt%, and Ti is 0.05～0.2wt%, P＜0.015wt%, S＜0.010wt%, all the other are Fe and unavoidable impurities; Wherein, Si+Mn+Cr+Mo+Al≤6.00wt%, Nb+Ti≤0.30wt%.
The tensile strength of the superstrength nanostructure dual phase steel of present embodiment manufacturing is 2100～2500MPa, and hardness is 600～680HV, and unit elongation is 17～27%, and fracture toughness is 23～33MPam
1/2Superstrength nanostructure dual phase steel.
Embodiment 3
A kind of superstrength dual phase steel and manufacture method thereof of nanostructure.Earlier with steel billet austenitizing 0.3～0.6 hour under 850～1000 ℃ of conditions; Under the condition of 0～60 ℃ of water-bath, quench then, be incubated 1.0～7.0 minutes; Carry out carbon distribution+tempering afterwards under the condition of 330～530 ℃ salt bath, the time is 0.01～0.65 hour; Last shrend is to room temperature.
The chemical ingredients and the content thereof of steel billet are: C is 0.80～1.00wt%, Si is 1.20～1.70wt%, Mn is 1.30～1.80wt%, and Cr is 1.00～1.60wt%, and Mo is 0.10～0.60wt%, Al is 0.10～0.60wt%, Ti is 0.05～0.2wt%, and V is 0.05～0.2wt%, P＜0.015wt%, S＜0.010wt%, all the other are Fe and unavoidable impurities; Wherein, Si+Mn+Cr+Mo+Al≤5.00wt%, Ti+V≤0.30wt%.
The tensile strength of the superstrength nanostructure dual phase steel of present embodiment manufacturing is 2150～2550MPa, and hardness is 630～700HV, and unit elongation is 15～25%, and fracture toughness is 20～30MPam
1/2Superstrength nanostructure dual phase steel.
Embodiment 4
A kind of superstrength dual phase steel and manufacture method thereof of nanostructure.Earlier with steel billet austenitizing 0.3～0.6 hour under 850～1000 ℃ of conditions; Under the condition of 10～70 ℃ of water-baths, quench then, be incubated 1.0～8.0 minutes; Carry out carbon distribution+tempering afterwards under the condition of 300～500 ℃ salt bath, the time is 0.1～0.75 hour; Last shrend is to room temperature.
The chemical ingredients and the content thereof of steel billet are: C is 0.78～1.00wt%, Si is 1.20～1.80wt%, Mn is 1.20～1.80wt%, Cr is 1.00～1.60wt%, and Mo is 0.20～0.80wt%, and Al is 0.20～0.80wt%, Ti is 0.05～0.2wt%, P＜0.015wt%, S＜0.010wt%, all the other are Fe and unavoidable impurities; Wherein, Si+Mn+Cr+Mo+Al≤6.00wt%.
The tensile strength of the superstrength nanostructure dual phase steel of present embodiment manufacturing is 2100～2450MPa, and hardness is 610～680HV, and unit elongation is 18～25%, and fracture toughness is 22～30MPam
1/2Superstrength nanostructure dual phase steel.
Owing to adopt technique scheme, the microstructure of the superstrength nanostructure dual phase steel of this embodiment manufacturing is that the martensite lath of nano level (～100nm thickness) is a matrix, the distributing super fine organization of carbide of retained austenite and nano-scale (～10nm diameter) of disperse.The volume fraction of retained austenite accounts for bigger ratio (10～40vol%).The lath martensite tissue of nanostructure, toughness and breaking resistance with superelevation; Austenite is the toughness phase, be distributed on the martensite lath or between the lath, be subjected under the external force effect viscous deformation taking place, absorb and consumed energy, delay the expansion of crackle, extremely beneficial to the toughness that improves sheet material, stress can undergo phase transition induced plasticity effect (TRIP effect) when big, further improves the toughness of steel; The carbide of nano-scale further increases its intensity.Because of the solution strengthening of carbon, dislocations strengthening, martensite lath are strengthened, induced plasticity is strengthened, the precipitation strength of carbide etc., make this steel can reach the intensity rank of superelevation; Distribute because of retained austenite becomes fine strip shape, and volume content is bigger, makes this steel reach good plasticity rank, its comprehensive mechanical property excellence.
The tensile strength of the superstrength nanostructure dual phase steel of this embodiment manufacturing is that 1800～2550MPa, hardness are that 550～700HV, unit elongation are 15～30%, fracture toughness is 20～35MPam
1/2The superstrength nanostructure dual phase steel of manufacturing is with respect to the nanostructure bainitic steel, and not only its heat treatment time shortens greatly, and its intensity, hardness, plasticity, toughness is higher than or be equivalent to the nanostructure bainitic steel; With respect to the nanostructure martensitic steel of low-carbon (LC) and middle carbon, its intensity and hardness significantly improve, and plasticity and toughness also are higher than other steel grades of analogous components.
Therefore, the characteristics that this embodiment has is with low cost, technology is simple and heat treatment cycle is short, prepared plate property is good, can be widely used in making undercarriage and girder, solid rocket motor case, supercentrifuge rotary barrel and other bear heavily stressed structure unit.
Claims (3)
1. the manufacture method of the superstrength dual phase steel of a nanostructure is characterized in that earlier steel billet austenitizing 0.2～0.6 hour under 850～1050 ℃ of conditions; Under 0～100 ℃ of condition, carry out water-bath again and quench, be incubated 1.0～10.0 minutes; Carry out carbon distribution+tempering then under 300～600 ℃ of conditions, the time is 0.01～1.0 hour; Last shrend is to room temperature;
The chemical ingredients and the content thereof of steel billet are: C is 0.71～1.00wt%, Si is 1.00～2.00wt%, and Mn is 1.00～2.00wt%, and Cr is 1.00～1.60wt%, Mo is 0.05～1.00wt%, Al is 0.05～1.00wt%, and Nb is 0.00～0.2wt%, and Ti is 0.00～0.2wt%, V is 0.00～0.2wt%, P＜0.015wt%, S＜0.010wt%, all the other are Fe and unavoidable impurities; Wherein, Si+Mn+Cr+Mo+Al≤6.00wt%, Nb+Ti+V≤0.30wt%.
2. the manufacture method of the superstrength dual phase steel of nanostructure according to claim 1 is characterized in that described carbon distribution+tempered medium is a kind of in salt bath, inert atmosphere and the faint reducing atmosphere.
3. according to the superstrength dual phase steel of the nanostructure of the manufacture method manufacturing of the superstrength dual phase steel of each described nanostructure in the claim 1～2.
Priority Applications (2)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN 201110042031 CN102127711B (en) | 2011-02-22 | 2011-02-22 | Nano-structured ultrahigh-strength dual-phase steel and production method thereof |
| PCT/CN2011/075639 WO2012113188A1 (en) | 2011-02-22 | 2011-06-13 | Nanostructured ultra-strength dual-phase steel and producing method thereof |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN 201110042031 CN102127711B (en) | 2011-02-22 | 2011-02-22 | Nano-structured ultrahigh-strength dual-phase steel and production method thereof |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN102127711A true CN102127711A (en) | 2011-07-20 |
| CN102127711B CN102127711B (en) | 2012-05-23 |
Family
ID=44265977
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN 201110042031 Expired - Fee Related CN102127711B (en) | 2011-02-22 | 2011-02-22 | Nano-structured ultrahigh-strength dual-phase steel and production method thereof |
Country Status (2)
| Country | Link |
|---|---|
| CN (1) | CN102127711B (en) |
| WO (1) | WO2012113188A1 (en) |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102758207A (en) * | 2012-06-29 | 2012-10-31 | 上海市机械制造工艺研究所有限公司 | Complex heat treatment technology capable of improving surface performance of steel workpiece |
| CN109680126A (en) * | 2017-10-18 | 2019-04-26 | 赛峰起落架系统公司 | A method of processing steel |
Families Citing this family (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN107227433A (en) * | 2017-05-26 | 2017-10-03 | 中北大学 | A kind of high-performance martensitic-austenitic dual phase steel and preparation method thereof |
Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US4544422A (en) * | 1984-04-02 | 1985-10-01 | General Motors Corporation | Ferrite-austenite dual phase steel |
| CN101225499A (en) * | 2008-01-31 | 2008-07-23 | 上海交通大学 | Low-alloy super-strength multiphase steel and heat treatment method thereof |
Family Cites Families (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2004022794A1 (en) * | 2002-09-04 | 2004-03-18 | Colorado School Of Mines | Method for producing steel with retained austenite |
-
2011
- 2011-02-22 CN CN 201110042031 patent/CN102127711B/en not_active Expired - Fee Related
- 2011-06-13 WO PCT/CN2011/075639 patent/WO2012113188A1/en active Application Filing
Patent Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US4544422A (en) * | 1984-04-02 | 1985-10-01 | General Motors Corporation | Ferrite-austenite dual phase steel |
| CN101225499A (en) * | 2008-01-31 | 2008-07-23 | 上海交通大学 | Low-alloy super-strength multiphase steel and heat treatment method thereof |
Non-Patent Citations (1)
| Title |
|---|
| 《热处理》 20080430 徐祖耀 用于超高强度钢的淬火-碳分配-回火(沉淀) ( Q-P-T)工艺 1-4 1-3 , 第2期 2 * |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102758207A (en) * | 2012-06-29 | 2012-10-31 | 上海市机械制造工艺研究所有限公司 | Complex heat treatment technology capable of improving surface performance of steel workpiece |
| CN109680126A (en) * | 2017-10-18 | 2019-04-26 | 赛峰起落架系统公司 | A method of processing steel |
Also Published As
| Publication number | Publication date |
|---|---|
| CN102127711B (en) | 2012-05-23 |
| WO2012113188A1 (en) | 2012-08-30 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN101603119B (en) | Method for manufacturing steel plate with high strength and high toughness by using hot-rolling coiled plate | |
| CN104328360B (en) | Double-phase twinborn induced plastic super-strength automobile steel plate and preparation method thereof | |
| CN101624683B (en) | Ultra-high strength bainite rail steel and manufacturing method thereof | |
| CN103276312B (en) | High-strength steel plate having extra thickness of 80-120mm and method for producing same from continuous casting billet | |
| CN110029274A (en) | A kind of 1600MPa grades of High-strength high-plasticity drop stamping steel and preparation method thereof | |
| CN102337480B (en) | Ultra-high strength steel plate with excellent environmental embrittlement resistance and fatigue resistance, and manufacturing method thereof | |
| CN103422021B (en) | Low-yield-ratio structural steel with yield ratio equal to or larger than 550MPa and manufacturing method thereof | |
| CN101633996B (en) | 700MPa-grade high strength and high toughness hardened and tempered steel plate with low cost and manufacturing method thereof | |
| CN102965568B (en) | Phase toughness Low Alloy Steel Plate and preparation method thereof | |
| CN103343281A (en) | Lamellar double-phase high-strength and high-toughness steel and preparation method thereof | |
| CN102699031B (en) | 900 MPa grade ultrahigh-toughness low alloy steel and manufacture method thereof | |
| CN103555896B (en) | A kind of ultrahigh-intensity high-toughness multistep Isothermal Bainite steel and preparation method thereof | |
| EP4317512A1 (en) | Low-carbon, low-alloy and high-formability dual-phase steel having tensile strength of greater than or equal to 590 mpa, hot-dip galvanized dual-phase steel, and manufacturing method therefor | |
| CN103160667B (en) | High-strength intermediate-carbon ultrafine bainitic steel and preparation method thereof | |
| KR20230166081A (en) | Low-carbon, low-alloy Q&P steel or hot-dip galvanized Q&P steel with a tensile strength of 1180 MPa or more and manufacturing method thereof | |
| CN101403076B (en) | Composite reinforced high-ductility ultrahigh-strength secondary hardening steel | |
| CN108048741A (en) | hot rolled bainite steel rail and preparation method thereof | |
| CN110358970B (en) | Welded structure bainite high-strength steel with yield strength of 1100MPa and preparation method thereof | |
| CN102127711B (en) | Nano-structured ultrahigh-strength dual-phase steel and production method thereof | |
| JP2014525987A (en) | Wire rod excellent in hydrogen delayed fracture resistance, method for producing the same, high strength bolt using the same, and method for producing the same | |
| CN101624682B (en) | Ultra-high strength high-ductility steel and manufacturing method thereof | |
| CN115181884B (en) | 1280 MPa-level low-carbon low-alloy hot dip galvanized Q & P steel and rapid heat treatment hot dip galvanizing manufacturing method | |
| CN115181898B (en) | 1280 MPa-level low-carbon low-alloy Q & P steel and rapid heat treatment manufacturing method thereof | |
| CN101624684B (en) | Carburizing bainite steel and manufacturing method thereof | |
| JPH01259121A (en) | Manufacture of ultrahigh strength steel stock excellent in ductility |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| C06 | Publication | ||
| PB01 | Publication | ||
| C10 | Entry into substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| C14 | Grant of patent or utility model | ||
| GR01 | Patent grant | ||
| CF01 | Termination of patent right due to non-payment of annual fee |
Granted publication date: 20120523 Termination date: 20150222 |
|
| EXPY | Termination of patent right or utility model |