CN110066967A - A kind of preparation method of high-intensitive and surface quality non-hardened and tempered steel - Google Patents
A kind of preparation method of high-intensitive and surface quality non-hardened and tempered steel Download PDFInfo
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- CN110066967A CN110066967A CN201910472130.8A CN201910472130A CN110066967A CN 110066967 A CN110066967 A CN 110066967A CN 201910472130 A CN201910472130 A CN 201910472130A CN 110066967 A CN110066967 A CN 110066967A
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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
- C21D1/19—Hardening; Quenching with or without subsequent tempering by interrupted quenching
- C21D1/20—Isothermal quenching, e.g. bainitic hardening
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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
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0226—Hot rolling
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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
- C22C38/005—Ferrous alloys, e.g. steel alloys containing rare earths, i.e. Sc, Y, Lanthanides
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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
- 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
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel 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
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel 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
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
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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
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel 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
- C21D2211/002—Bainite
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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
- C21D2211/005—Ferrite
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- Crystallography & Structural Chemistry (AREA)
- Heat Treatment Of Steel (AREA)
Abstract
The present invention relates to a kind of preparation methods of high-intensitive and surface quality non-hardened and tempered steel, belong to field of metallurgy.A kind of preparation method of high-intensitive and surface quality non-hardened and tempered steel, include the steps that heat preservation and rolling, the rolling include the rolling in two stages of recrystallization zone and Unhydrated cement, wherein, recrystallization zone rolling: start rolling temperature is 1100~1150 DEG C, and finishing temperature is 950~1000 DEG C；Unhydrated cement rolling: 860~900 DEG C of start rolling temperature, 800~840 DEG C of finishing temperature, gained steel are cooled to 450~650 DEG C of progress bainitic transformations, upper cold bed slow cooling to room temperature with 30 DEG C/s~50 DEG C/s cooling rate after rolling.The method of the invention has greatly saved the energy and production cycle, shortens production producing line arrangement, and the equipment such as heat-treatment furnace for having simplified the later period, reduces production cost, reduce environmental pollution.
Description
Technical field
The present invention relates to a kind of preparation methods of high-intensitive and surface quality non-hardened and tempered steel, belong to field of metallurgy.
Background technique
With advancing by leaps and bounds for auto manufacturing, China, until present after 10 years since 2009, China is kept
The status of automobile production country the biggest in the world.Although being gradually saturated along with market, from 2011 to 2018 speedups by flying
Speed increases to slowdown in growth, and auto output 27,800,000 in 2018, having prediction to be promoted in 2019 even can break through 28,000,000
Amount.Engine plays the same effect of human body cardiac in the car, and also where the core of exactly entire automobile, crankshaft is hair again
Most important components in motivation, it can connect connecting rod stress under engine behavior and carry out turning Qu Yundong, by torque
Output is converted to power, due to working under the operating condition of a closed high temperature, while will receive rotation centrifugal force, air oil
The collective effects such as gas burning eruption inertia force, so rigidity, surface quality has relatively high performance to refer to for the intensity of crankshaft
Mark requires.In the normal work of automobile engine, since crankshaft-and-connecting-rod moves back and forth, abrasive grain or hard between connector
Micro-bulge and material surface interactions can generate the surface abrasion of crankshaft.Traditional automobile crane is with the quenched steel such as 40Cr
Make, but due to low-carbon steel bar lower cutting speed carry out processing will appear Integrated Chip or generate squama thorn the phenomenon that,
To make the crankshaft surface roughness after machine-shaping obviously deteriorate and then affect the final surface quality for processing finished product.It is cutting
Sharpener head and processed bar make material surface that plastic deformation and Vibration Condition occur when cutting extrusion friction also will increase slightly
Rugosity.
In traditional easy-cutting untempered steel, S constituent content is larger, can reduce interfacial tension, and hot-working character reduces, and is easy
It skids and cracks.Sulfide brittle temperature (830~1050 DEG C), it is (molten that S generates simple substance FeS in conjunction with the Fe in steel
1190 DEG C of point) or low melting point eutectic mixture FeS+FeO (980 DEG C of fusing point), addition Mn element affinity ratio Fe is strong, can be formed
MnS (1620 DEG C of fusing point), but can not seize completely, ratio 45:5, therefore temperature should be selected above 1200 DEG C in heating furnace
So that FeS is melted in surface completely, due to the presence of MnS, often forms strip in steel after rolling, easily become crackle
Source adversely affects performance, sulfide modified to carry out by ingredient improvement addition Rare-Earth Ce, forms bulk or imitative cone
Shape facilitates the toughness for promoting steel, reduces the cracks caused by MnS.Non-hardened and tempered steel does not pass through modulation treatment, power
It is lower to learn performance, finally tissue is pearlite and ferrite under traditional technique, by the way that the pre-heat treatment is added before hot rolling, after hot rolling
Ultrafast isothermal transformation after being as cold as bainite transformation temperature is added, the laggard excess of imports is cooled to room temperature fastly, prepares bainite ferrite group
Non-hardened and tempered steel is knitted, tensile strength, the mechanical properties such as hardness are promoted.
Summary of the invention
The object of the present invention is to provide a kind of preparation method of high-intensitive and surface quality non-hardened and tempered steel is above-mentioned to solve
Problem.
A kind of preparation method of high-intensitive and surface quality non-hardened and tempered steel, includes the steps that heat preservation and rolling, described to roll
System includes the rolling in two stages of recrystallization zone and Unhydrated cement, wherein
Recrystallization zone rolling: start rolling temperature is 1100~1150 DEG C, and finishing temperature is 950~1000 DEG C；
Unhydrated cement rolling: 860~900 DEG C of start rolling temperature, 800~840 DEG C of finishing temperature, by gained steel after rolling
450~650 DEG C of progress bainitic transformations, upper cold bed slow cooling to room temperature are cooled to 30 DEG C/s~50 DEG C/s cooling rate.
The non-hardened and tempered steel batch components are by weight percentage: C:0.18~0.22%, Mn:1.80~2.20%, Si:
0.35~0.40%, Cr:0.50~0.55%, Ni:0.05~0.08%, V:0.10~0.13%, Nb:0.05~0.08%,
Ti:0.013~0.015%, Ce:0.010~0.012%, surplus are Fe and inevitable impurity.
Steel of the present invention are bainite ferrite non-hardened and tempered steel by the final tissue that preparation process obtains.
The preparation method of of the present invention high-intensitive and surface quality non-hardened and tempered steel, by the improvement of chemical component,
Lanthanide series cerium is added in the non-hardened and tempered steel of conventional components, by the unique property of rare earth element, changes the folder in non-hardened and tempered steel
Sundries form, is become that size is small and field trash is precipitated in the round of Dispersed precipitate from larger-size corynebacterium.This heterogeneous structure
Non-hardened and tempered steel ingredient is by weight percentage: C:0.18~0.22%, Mn:1.80~2.20%, Si:0.35~0.40%, Cr:
0.50~0.55%, Ni:0.05~0.08%, V:0.10~0.13%, Nb:0.05~0.08%, Ti:0.013~
0.015%, Ce:0.010~0.012%, surplus are Fe and inevitable impurity.Specifically, in smelting process, in steel
0.010~0.012% Ce is added, is mingled with by the rare earth modified compound package of formation, changes the form of MnS effectively
It is kind, it is wide than reduction, formation circle or spindle to compare original diameter.After size is precipitated to a certain degree in control, moreover it is possible to become
In later period cooling procedure, the nucleation mass point of acicular ferrite when bainite isothermal phase change.
The preparation method of high-intensitive and surface quality non-hardened and tempered steel of the present invention rolls start rolling temperature in recrystallization zone
It is 1100~1150 DEG C, finishing temperature is 950~1000 DEG C, and Unhydrated cement rolls 860~900 DEG C of finishing temperatures of start rolling temperature
800~840 DEG C, to 450~650 DEG C, upper cold bed carries out bainite under the protection of insulation cover and turns 30 DEG C/s~50 DEG C/s water cooling
It is air-cooled to room temperature after lower cold bed after change, it is final to obtain bainite ferrite tissue non-hardened and tempered steel.
In the preparation method of high-intensitive and surface quality non-hardened and tempered steel of the present invention, the incubation step before the rolling
Are as follows: blank is put into heating furnace and is heated to 1200~1300 DEG C, keeps the temperature 2.5~3h.
Stock of square is heated to 1200~1300 DEG C of 2.5~3h of heat preservation, avoids sulfide brittle temperature, simple substance
FeS (1190 DEG C of fusing point) or low melting point eutectic mixture FeS+FeO (980 DEG C of fusing point), addition Mn element affinity ratio Fe is strong, can
It is formed MnS (1620 DEG C of fusing point), but Mn can not seize the S in FeS completely, and probably there remains S less than 10% still can be with
Fe is combined, therefore temperature should be selected above 1200 DEG C FeS is made to be melted in surface completely in heating furnace.
Further, the milling step carries out 5 passes altogether, wherein preceding 3 passage is recrystallization zone rolling, pressure
Rate is respectively 25%, 30%, 35%；2 passages are Unhydrated cement rolling afterwards, and reduction ratio is respectively 40% and 30%.
Further, recrystallization zone rolls: 3 passages of rolling, reduction ratio is respectively 25%, 30%, 35%, start rolling temperature
It is 1100~1150 DEG C, finishing temperature is 950~1000 DEG C.
Further, Unhydrated cement rolls: 2 passages of rolling, reduction ratio is respectively 40% and 30%, start rolling temperature
860~900 DEG C, 800~840 DEG C of finishing temperature.
Further, after rolling by gained blank with 30 DEG C/s~50 DEG C/s cooling rate be cooled to 450~650 DEG C into
Row bainitic transformation, upper cold bed are cooled to room temperature with 1 DEG C~3 DEG C/s cooling rate.
Further, after heat preservation, peeling is included the steps that before rolling: dephosphorization is added in the blank after heat preservation before the rolling
Equipment removes scale on surface by hydraulic pressure.Dephosphorization equipment is added after heating furnace, use is uniformly injected in slab up and down
On, the effective hitting power for borrowing water gets rid of the iron scale in heating process, and iron scale in course of hot rolling is prevented to be pressed into
Surface forms pockmark, and surface quality is caused to decline.And reduce the temperature of casting billet surface, formed the core table temperature difference, blooming mill compared with
Under large deformation parameter, the defects of promoting core deformation increase, effectively mitigate loose shrinkage cavity, keep tissue more uniform.
Further, dephosphorization equipment of the present invention is high pressure water dephosphorization equipment, commercially available, preferably its device length
2~3m, 1000~1500m of equipment water3/hr；Cooling nozzles are distributed spacing 400mm along rolling to 15~20 °.
A preferred technical solution of the invention are as follows: a kind of preparation method of high-intensitive and surface quality non-hardened and tempered steel,
It is smelted into vacuum electric induction furnace and forges squarely base after ingot casting, blank is put into heating furnace and is heated to 1200~
1300 DEG C, after keeping the temperature 2.5~3h, dephosphorization equipment is added before hot rolling and removes scale on surface by hydraulic pressure, is sent into roughing
Unit is rolled, and it is 1100~1150 DEG C that recrystallization zone, which rolls start rolling temperature, and finishing temperature is 950~1000 DEG C, is not tied again
Crystalline region rolls 860~900 DEG C of start rolling temperature, 800~840 DEG C of finishing temperature, is quickly cooled to steel into Ultrafast cooling device
450~650 DEG C of progress bainitic transformations, 1 DEG C of upper cold bed~3 DEG C/s cooling rate are cooled to room temperature,
Wherein, non-hardened and tempered steel batch components are by weight percentage: C:0.18~0.22%, Mn:1.80~2.20%, Si:
0.35~0.40%, Cr:0.50~0.55%, Ni:0.05~0.08%, V:0.10~0.13%, Nb:0.05~0.08%,
Ti:0.013~0.015%, Ce:0.010~0.012%, surplus are Fe and inevitable impurity.
The method controls the form of material phase transformation and precipitation field trash to the present invention through the above technical solution, can
To significantly improve the surface roughness of finished steel, the surface quality of product is promoted.
The present invention utilizes the intensity and surface quality of following three process control non-hardened and tempered steels.
First step heating process: as cast condition blank being placed in heating furnace and is heated to 1200~1300 DEG C, keeps the temperature 2.5~3h
Afterwards, scale on surface is removed by dephosphorization apparatus, heat treatment will promote austenite forming core cementite complete in blank tissue
Dissolution, which reaches austenitizing, makes internal component reach homogenization.
Second step course of hot rolling: the blank after heat treatment is carried out just in 1100~1150 DEG C of austenite recrystallization areas
It rolls, by moderate finite deformation amount, core deformation is promoted to increase, promote the defects of structural homogenity eliminates loose shrinkage cavity and generate.950
~1000 DEG C of completion recrystallization zone rollings.860~900 DEG C of start rolling temperature, 800~840 DEG C of finishing temperature is rolled in Unhydrated cement
Carry out finish rolling.Promote Ferrite Deformation refinement, increase the deformation energy storage in steel, to effectively promote M (C, N) precipitation, increases
The nucleation mass point of bainite ferrite and acicular ferrite.
Third step cooling procedure: the steel after finish rolling out are subjected to supper-fast water-cooled cooling to 450~650 DEG C, by adding
Quickly cooling but prevents granular ferrite generation from growing up, refining grain size.And insulation cover is installed on cold bed and carries out Isothermal Bainite
Transformation carries out air-cooled being cooled to room temperature out after cold bed.
The invention has the benefit that the method for the invention is mingled with by the rare earth modified compound package of formation, make MnS
Form be effectively improved, it is wide than reducing to compare original diameter, forms round or spindle.The MnS of formation can be in the later period
The edge of a knife is lubricated in cutting process, the dephosphorization apparatus of big yield is added before roughing, can get rid of the oxidation of high temperature generation
The defects of iron sheet increases the blank core table temperature difference, promotes core deformation by the breaking down of aximal deformation value, reduces loose shrinkage cavity, makes ingredient
It is more uniform.Ultra-rapid cooling is carried out after finish rolling finish to gauge effectively avoids austenite from carrying out perlitic transformation, avoids pro-eutectoid
Transformation ferrite is grown up, and is directly cooled to bainite transformation temperature and is kept the temperature, reaches the bainite transformation content being pre-designed
Afterwards, cold bed is air-cooled to room temperature out, acicular ferrite nucleating will be promoted to grow up, and effectively refined bainite size, thus
Promote the toughness of integral material.Reach same mechanical property with the comparison of traditional quenched and tempered steel, and saves quenched and tempered steel in hot rolling
The process for also carrying out quenching and high tempering heat treatment afterwards, has greatly saved the energy, has saved the production cycle, shortened
Producing line arrangement, and the equipment such as heat-treatment furnace for having simplified the later period are produced, production cost is reduced, reduces environmental pollution.
Detailed description of the invention
Fig. 1 is the preparation method process flow chart of high-intensitive and surface quality non-hardened and tempered steel of the present invention；
Fig. 2 (a)~(c) is the room temperature metallographic microstructure shape appearance figure of Examples 1 to 3 products obtained therefrom；Fig. 2 shows embodiment
The room temperature microstructure of 1~3 products obtained therefrom is bainite and martensite tissue, and there are also a small amount of ferrites.
Fig. 3 (a)~(c) is that MnS scanning electron microscope displaing micro tissue topography figure is precipitated in Examples 1 to 3；Fig. 3 display embodiment 1~
3 products obtained therefroms have MnS existing for glomeration between crystal boundary.
Fig. 4 (a)~(c) is the three-dimensional surface shape of Examples 1 to 3 products obtained therefrom and (d)~(f) is that corresponding surface is thick
Rugosity datagram.
Specific embodiment
Following non-limiting embodiments can with a person of ordinary skill in the art will more fully understand the present invention, but not with
Any mode limits the present invention.
Test method described in following embodiments is unless otherwise specified conventional method；The reagent and material, such as
Without specified otherwise, commercially obtain.
" Ultrafast cooling device " used in following embodiments is that Authorization Notice No. is that CN202185466U China is practical new
" the rolling rear ultra-fast cooling device of Ultra Fast Cooling " of type patent disclosure.
Dephosphorization process described in following embodiments carries out in high pressure water dephosphorization equipment, sets before furnace outlet and rolling
Set dephosphorization equipment, specially process conditions are as follows: device length 2m, equipment water 1500m3/hr；Cooling nozzles are divided along rolling to 20 °
Cloth spacing 400mm.
Embodiment 1
Non-hardened and tempered steel 1# is rolled using method proposed by the present invention, slab thickness 80mm, by blank (C:0.20%,
Mn:2.00%, Si:0.35%, Cr:0.50%, Ni:0.06%, V:0.12%, Nb:0.05%, Ti:0.013%, Ce:
0.010%, surplus is Fe and inevitable impurity.) be put into heating furnace and be heated to 1200 DEG C, keep the temperature carry out after 3h dephosphorization and
Rolling, it is 1125 DEG C that recrystallization zone, which rolls start rolling temperature, and finishing temperature is 956 DEG C, and point three passages are rolled, reduction ratio difference
It is 25%, 30%, 35%.Unhydrated cement rolls 859 DEG C of start rolling temperature, 840 DEG C of finishing temperature, and two passages is divided to be rolled, and presses
Lower rate is respectively 40%, 30%.It is rolled into the steel plate of 10mm, be cooled to 654 DEG C into Ultrafast cooling device, it is rear air-cooled
To room temperature.
Embodiment 2
Non-hardened and tempered steel 2# is rolled using method proposed by the present invention, slab thickness 80mm, by blank (C:0.20%,
Mn:2.00%, Si:0.35%, Cr:0.50%, Ni:0.06%, V:0.12%, Nb:0.05%, Ti:0.013%, Ce:
0.010%, surplus is Fe and inevitable impurity.) be put into heating furnace and be heated to 1200 DEG C, keep the temperature carry out after 3h dephosphorization and
Rolling, it is 1128 DEG C that recrystallization zone, which rolls start rolling temperature, and finishing temperature is 964 DEG C, and point three passages are rolled, reduction ratio difference
It is 25%, 30%, 35%.Unhydrated cement rolls 852 DEG C of start rolling temperature, 841 DEG C of finishing temperature, and two passages is divided to be rolled, and presses
Lower rate is respectively 40%, 30%.It is rolled into the steel plate of 10mm, be cooled to 546 DEG C into Ultrafast cooling device, it is rear air-cooled
To room temperature.
Embodiment 3
Non-hardened and tempered steel 3# is rolled using method proposed by the present invention, slab thickness 80mm, by blank (C:0.20%,
Mn:2.00%, Si:0.35%, Cr:0.50%, Ni:0.06%, V:0.12%, Nb:0.05%, Ti:0.013%, Ce:
0.010%, surplus is Fe and inevitable impurity.) be put into heating furnace and be heated to 1200 DEG C, keep the temperature carry out after 3h dephosphorization and
Rolling, it is 1142 DEG C that recrystallization zone, which rolls start rolling temperature, and finishing temperature is 964 DEG C, and point three passages are rolled, reduction ratio difference
It is 25%, 30%, 35%.Unhydrated cement rolls 871 DEG C of start rolling temperature, 852 DEG C of finishing temperature, and two passages is divided to be rolled, and presses
Lower rate is respectively 40%, 30%.It is rolled into the steel plate of 10mm, be cooled to 461 DEG C into Ultrafast cooling device, it is rear air-cooled
To room temperature.
The surface hardness table of Examples 1 to 3 products obtained therefrom
The surface roughness of Examples 1 to 3 products obtained therefrom
Roughness parameter shown in Fig. 4 (a)
(b) roughness parameter shown in Fig. 4
(c) roughness parameter shown in Fig. 4
Claims (6)
1. a kind of preparation method of high-intensitive and surface quality non-hardened and tempered steel, it is characterised in that: including the step for keeping the temperature and rolling
Suddenly, the rolling includes the rolling in two stages of recrystallization zone and Unhydrated cement, wherein
Recrystallization zone rolling: start rolling temperature is 1100~1150 DEG C, and finishing temperature is 950~1000 DEG C；
Unhydrated cement rolling: 860~900 DEG C of start rolling temperature, 800~840 DEG C of finishing temperature, by gained steel with 30 after rolling
DEG C/s~50 DEG C/s cooling rate is cooled to 450~650 DEG C of progress bainitic transformations, upper cold bed slow cooling to room temperature.
The non-hardened and tempered steel batch components are by weight percentage: C:0.18~0.22%, Mn:1.80~2.20%, Si:0.35~
0.40%, Cr:0.50~0.55%, Ni:0.05~0.08%, V:0.10~0.13%, Nb:0.05~0.08%, Ti:
0.013~0.015%, Ce:0.010~0.012%, surplus are Fe and inevitable impurity.
2. according to the method described in claim 1, it is characterized by: incubation step before the rolling are as follows: blank is put into plus
It is heated to 1200~1300 DEG C in hot stove, keeps the temperature 2.5~3h.
3. according to the method described in claim 1, it is characterized by: the milling step carries out 5 passes altogether, wherein preceding 3
Passage is recrystallization zone rolling, and reduction ratio is respectively 25%, 30%, 35%；2 passages are Unhydrated cement rolling, reduction ratio afterwards
Respectively 40% and 30%.
4. according to the method described in claim 1, it is characterized by: Unhydrated cement rolls: 860~900 DEG C of start rolling temperature, eventually
800~840 DEG C of temperature are rolled, gained steel are cooled to 450~650 DEG C of progress with 30 DEG C/s~50 DEG C/s cooling rate after rolling
Bainitic transformation, upper cold bed are cooled to room temperature with 1 DEG C~3 DEG C/s cooling rate.
5. according to the method described in claim 1, it is characterized by: including the steps that peeling before rolling after heat preservation: keeping the temperature
Dephosphorization equipment is added before the rolling and removes scale on surface by hydraulic pressure for blank afterwards.
6. according to the method described in claim 1, it is characterized by: the final tissue of gained non-hardened and tempered steel is bainite ferrite
Non-hardened and tempered steel.
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| CN201910472130.8A CN110066967B (en) | 2019-05-31 | 2019-05-31 | Preparation method of non-quenched and tempered steel with high strength and surface quality |
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Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN110468268A (en) * | 2019-09-05 | 2019-11-19 | 首钢集团有限公司 | A kind of rolling mill practice improving non-hardened and tempered steel wearability and toughness |
| CN112210723A (en) * | 2020-10-28 | 2021-01-12 | 湖南华菱湘潭钢铁有限公司 | Production method of atmospheric corrosion resistant steel |
| CN113388774A (en) * | 2021-05-27 | 2021-09-14 | 本钢板材股份有限公司 | Hot-rolled air-cooled bainite high-toughness high-strength steel plate with tensile strength of more than or equal to 1300MPa and manufacturing method thereof |
| CN114058943A (en) * | 2021-09-14 | 2022-02-18 | 武汉钢铁有限公司 | Microalloyed steel and manufacturing method thereof |
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Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
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| CN110468268A (en) * | 2019-09-05 | 2019-11-19 | 首钢集团有限公司 | A kind of rolling mill practice improving non-hardened and tempered steel wearability and toughness |
| CN110468268B (en) * | 2019-09-05 | 2021-08-17 | 首钢集团有限公司 | Rolling process for improving wear resistance and toughness of non-quenched and tempered steel |
| CN112210723A (en) * | 2020-10-28 | 2021-01-12 | 湖南华菱湘潭钢铁有限公司 | Production method of atmospheric corrosion resistant steel |
| CN113388774A (en) * | 2021-05-27 | 2021-09-14 | 本钢板材股份有限公司 | Hot-rolled air-cooled bainite high-toughness high-strength steel plate with tensile strength of more than or equal to 1300MPa and manufacturing method thereof |
| CN114058943A (en) * | 2021-09-14 | 2022-02-18 | 武汉钢铁有限公司 | Microalloyed steel and manufacturing method thereof |
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|---|---|
| CN110066967B (en) | 2020-12-15 |
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