CN106834941A - A kind of hot press-formed steel and its production method - Google Patents
A kind of hot press-formed steel and its production method Download PDFInfo
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- CN106834941A CN106834941A CN201710042303.3A CN201710042303A CN106834941A CN 106834941 A CN106834941 A CN 106834941A CN 201710042303 A CN201710042303 A CN 201710042303A CN 106834941 A CN106834941 A CN 106834941A
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- hot press
- formed steel
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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
-
- 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
-
- 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
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
- C21D8/0273—Final recrystallisation annealing
-
- 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
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
-
- 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
- C22C38/06—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
- C22C38/28—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
- C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
-
- 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
- C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur
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- 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 Sheet Steel (AREA)
Abstract
The invention discloses a kind of hot press-formed steel and its production method, it includes heating, hot rolling, cold rolling, continuous annealing and smooth operation；The weight/mass percentage composition of the strand composition that the hot rolling is used is C 0.18~0.25%, Mn 1.00~1.50%, Si 0.15~0.40%, P≤0.020%, S≤0.005%, Cr 0.10~0.30%, Ti 0.010~0.050%, Alt 0.020~0.060%, B 15ppm~50ppm, [N]≤40ppm, remaining is Fe and inevitable impurity.Method of this method by controlling hot rolling, cold rolling and continuous annealing and the technological parameter such as smooth to produce hot stamping steel, small with enforcement difficulty, cost is relatively low, stable production process, the characteristics of end properties are excellent；Production cost, improve production efficiency can effectively be reduced.Hot press-formed steel is produced using continuous annealing process, cost-effective, properties of product stabilization high compared with cover annealing production efficiency.
Description
Technical field
The present invention relates to a kind of automobile high-strength steel, especially a kind of hot press-formed steel and its production method.
Background technology
With the proposition of automotive light weight technology, the development rate of automobile high-strength steel is accelerated, be steel industry Transformation Development
There is provided chance and challenge.In order to reduce white body deadweight, in body of a motor car manufacture, the use ratio of high-strength steel is increasingly
Height, while punching press new technology is also constantly suggested and applies.For take into account lightweight, crashworthiness, high intensity stamping parts return
The problems such as bullet and die wear, hot press-formed steel and forming technique are arisen at the historic moment.Arcelor companies develop first and batch is raw
Hot press-formed steel plate Usibor1500 is produced.It is characterized in after roll forming, material structure is uniform ferrite+pearl
Body of light, yield strength is 280~400MPa, and tensile strength is more than 450MPa.After Overheating Treatment, it is organized as uniform horse
Family name's body, up to 1200MPa, tensile strength, up to 1600MPa, is 3~4 times of general steel plate intensity to yield strength.Ensure that vapour
While car vehicle body security, by thinning vehicle body steel plate, Vehicle mass reduction is realized.
The current research on hot press-formed steel focuses mostly in follow-up drop stamping process aspect, and in practice to full
Sufficient drop stamping, the shearing blanking and preforming process of early stage is also extremely important, and it is good that this requires that hot forming base-material should have
Cold-workability.To reduce the production cost of iron and steel enterprise, suitable production technology should be used, and disclosure satisfy that the use of client will
Ask.Publication No. CN103469090A proposes a kind of method for annealing of high-strength hot forming steel, i.e., in two-phase section（α+γ）Protect
Warm 0.1-5h, is then cooled to a certain temperature of below A1 with the cooling velocity of 0.1-10 DEG C/s, 0.1-5h is incubated, finally with 0.1-10
DEG C/cooling velocity of s is cooled to room temperature.Although this method is than traditional cover annealing technique, annealing time is short, and actual production is come
Say relatively difficult to achieve.Therefore need badly it is a kind of can be with mass, low cost, the technique of the hot press-formed steel of steady production.
The content of the invention
The technical problem to be solved in the present invention is to provide a kind of hot press-formed steel with good cold-workability；This hair
It is bright to additionally provide a kind of low cost, the production method of the hot press-formed steel of mass.
In order to solve the above technical problems, the weight/mass percentage composition of present component is：C 0.18~0.25%, Mn 1.00~
1.50%, Si 0.15~0.40%, P≤0.020%, S≤0.005%, Cr 0.10~0.30%, Ti 0.010~0.050%, Alt
0.020~0.060%, B 15ppm~50ppm, [N]≤40ppm, remaining is Fe and inevitable impurity.
The present invention uses the function of alloying element as follows：
C：Play solution strengthening, determine the intensity of martensitic phase after quenching, that is, determine the final performance of hot press-formed steel.
Therefore, C content control is 0.18~0.25%.
Si：On the one hand the precipitation of carbide in steel can be suppressed, it is ensured that the carbon content of martensitic phase after quenching, on the other hand
By solution strengthening, the intensity of steel is improved, while Si too high levels can reduce the toughness plasticity of martensite steel.Therefore Si should be controlled
0.15~0.40%.
Mn：Quenching degree to improving steel is most strong, and the quenching degree of steel is ensured by adding more Mn elements, and Mn contents are excessive
The welding performance of steel can be reduced.Therefore, Mn contents should be controlled 1.00~1.50%.
Cr：The quenching degree of steel can be effectively improved and high temperature surface oxidation is prevented, but Cr too high levels can deteriorate adding for steel
Work performance.Therefore, Cr contents should be controlled 0.10~0.30%.
S：Inevitable impurity, forming Sulfide inclusion can deteriorate the performance of steel in grain boundaries segregation, therefore should control
System is below 0.005%.
N：Nitride is formed in steel, invigoration effect can be played, but excessive N can make the plasticity of steel and toughness reduction, therefore N
Should control in below 40ppm.
P：Easily in the grain boundaries segregation of steel, dramatically increase the tough fragility of steel, so that Delayed hydride cracking sensitiveness
Raise, therefore, P content should be controlled below 0.020%.
Al：Nitrogen agent is determined in deoxidation in smelting process, it can in addition contain play a part of high-temperature oxidation resistant, but excessive Al
Aluminate can be formed, deteriorates the performance of steel, therefore Al content should be controlled 0.020~0.060%.
Ti：Carbon, nitride are formed, precipitation strength on the one hand can be formed, on the other hand in steel austenitizing, can be played
The effect of Austenite Grain Growth is hindered, so as to ensure the intensity of steel after quenching.Therefore Ti contents should control 0.010~
0.050%。
B：There is obvious effect to the quenching degree of steel, while tiny boride is in grain boundaries segregation, strengthen crystal boundary, improve
The toughness of steel, but when the mass fraction of B is more than 50ppm, B can be made excessively to be separated out in grain boundaries, reduce the toughness of steel.Therefore, B
Content should be controlled in 15~50ppm.
The inventive method includes heating, hot rolling, cold rolling, continuous annealing and smooth operation；The strand that the hot rolling is used into
The weight/mass percentage composition for dividing is as described above.
The soaking temperature of heating process described in the inventive method is 1150~1250 DEG C, is 90~150 points in stove total time
Clock.
Hot-rolled process described in the inventive method：Cooled down using leading portion, finishing temperature is 850~900 DEG C, coiling temperature is
560~650 DEG C.
Cold roling reduction >=50% of cold rolling process described in the inventive method.
Continuous annealing operation described in the inventive method：780~830 DEG C of holding temperature, 100~200s of soaking time, slow cooling
650~700 DEG C of end temp, 400~450 DEG C of rapid cooling end temp, 370~400 DEG C of overaging temperature.
The smooth elongation percentage of smooth operation described in the inventive method is 0.6%~1.6%.
It is using the beneficial effect produced by above-mentioned technical proposal：Steel band of the present invention has good cold working shearing property
Can, surface quality is excellent, with low cost.
The inventive method produces heat and strikes out by controlling hot rolling, cold rolling and continuous annealing and the technological parameter such as smooth
The method of shape steel, small with enforcement difficulty, cost is relatively low, stable production process, the characteristics of end properties are excellent；Can effectively drop
Low production cost, improve production efficiency.Hot press-formed steel is produced using continuous annealing process, compared with cover annealing production efficiency
Height, cost-effective, properties of product stabilization.
The inventive method produces high-performance by adjusting component design, hot rolling, cold rolling, annealing and flattening technological parameter
Hot press-formed steel band；Properties of product are：Tensile strength extends between 500~700MPa, 300~500MPa of yield strength
Rate more than 20%；With good cold and hot formability and quenching degree, intensity rank can reach 1500MPa after shaping, with low resilience
Property, can effectively improve the precision of part.
Specific embodiment
With reference to specific embodiment, the present invention is further detailed explanation.
Embodiment 1~12：This hot press-formed steel is produced using following concrete technologies.
（1）Each embodiment is produced using the strand using chemical composition described in table 1.
Table 1：The chemical composition of the strand of embodiment 1~12（wt%）
（2）Technical process is：Heating → hot rolling → cold rolling → continuous annealing → smooth → batch storage, controls the parameter of each operation
It is as described below：Heating process uses stepped heating stove heat, and the heating-up temperature of soaking zone strand is 1150~1250 DEG C, in stove
Total time is 90~150 minutes；Hot-rolled process using leading portion cool down, finishing temperature be 850~900 DEG C, coiling temperature be 560~
650℃；Cold roling reduction >=50% of cold rolling process；780~830 DEG C of the holding temperature of continuous annealing operation, soaking time 100
~200s, 650~700 DEG C of slow cooling end temp, 400~450 DEG C of rapid cooling end temp, 370~400 DEG C of overaging temperature；It is flat
The smooth elongation percentage of whole operation is 0.6%~1.6%.The specific process parameter of each embodiment is shown in Table 2.
Table 2：The technological parameter of embodiment 1~12
（3）The hot press-formed steel of the gained of embodiment 1~12 carries out performance detection, and sample marking distance is 80mm, and the width of parallel-segment is
20mm, the mechanical property that detection is obtained is shown in Table 3.
Table 3：The mechanical property of the products obtained therefrom of embodiment 1~12
Claims (7)
1. a kind of hot press-formed steel, it is characterised in that the weight/mass percentage composition of its composition is：C 0.18~0.25%, Mn
1.00~1.50%, Si 0.15~0.40%, P≤0.020%, S≤0.005%, Cr 0.10~0.30%, Ti 0.010~
0.050%, Alt 0.020~0.060%, B 15ppm~50ppm, [N]≤40ppm, remaining is Fe and inevitable impurity.
2. a kind of production method of hot press-formed steel, it is characterised in that：It includes that heating, hot rolling, cold rolling, continuous annealing are peaceful
Whole operation；The weight/mass percentage composition of the strand composition that the hot rolling is used for：C 0.18~0.25%, Mn 1.00~1.50%, Si
0.15~0.40%, P≤0.020%, S≤0.005%, Cr 0.10~0.30%, Ti 0.010~0.050%, Alt 0.020~
0.060%, B 15ppm~50ppm, [N]≤40ppm, remaining is Fe and inevitable impurity.
3. the production method of a kind of hot press-formed steel according to claim 2, it is characterised in that the heating process
Soaking temperature is 1150~1250 DEG C, is 90~150 minutes in stove total time.
4. a kind of production method of hot press-formed steel according to claim 2, it is characterised in that the hot-rolled process：
Cooled down using leading portion, finishing temperature is 850~900 DEG C, coiling temperature is 560~650 DEG C.
5. the production method of a kind of hot press-formed steel according to claim 2, it is characterised in that：The cold rolling process
Cold roling reduction >=50%.
6. a kind of production method of hot press-formed steel according to claim 2, it is characterised in that the continuous annealing work
Sequence：780~830 DEG C of holding temperature, 100~200s of soaking time, 650~700 DEG C of slow cooling end temp, rapid cooling end temp
400~450 DEG C, 370~400 DEG C of overaging temperature.
7. the production method of a kind of hot press-formed steel according to claim 2-6 any one, it is characterised in that：Institute
The smooth elongation percentage for stating smooth operation is 0.6%~1.6%.
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| Application Number | Priority Date | Filing Date | Title |
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| CN201710042303.3A CN106834941A (en) | 2017-01-20 | 2017-01-20 | A kind of hot press-formed steel and its production method |
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| CN201710042303.3A CN106834941A (en) | 2017-01-20 | 2017-01-20 | A kind of hot press-formed steel and its production method |
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Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN108396224A (en) * | 2018-04-03 | 2018-08-14 | 河钢股份有限公司承德分公司 | A kind of hot press-formed ultra-thin hot-rolled strip steel and its production method |
| CN109628846A (en) * | 2018-12-20 | 2019-04-16 | 唐山钢铁集团有限责任公司 | 1300MPa grades of automobile super high tensile cold-rolled steel plates and its production method |
| CN110129670A (en) * | 2019-04-25 | 2019-08-16 | 首钢集团有限公司 | A kind of 1300MPa grades of High-strength high-plasticity drop stamping steel and preparation method thereof |
| CN110257702A (en) * | 2019-06-24 | 2019-09-20 | 鞍钢股份有限公司 | Steel for hot stamping forming and hot forming method thereof |
| CN111321341A (en) * | 2019-12-03 | 2020-06-23 | 马鞍山钢铁股份有限公司 | 1500 MPa-grade non-coating hot forming steel with low high-temperature friction coefficient and preparation method thereof |
| CN113528932A (en) * | 2021-05-31 | 2021-10-22 | 唐山钢铁集团高强汽车板有限公司 | Martensite steel plate and preparation method thereof |
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Cited By (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN108396224A (en) * | 2018-04-03 | 2018-08-14 | 河钢股份有限公司承德分公司 | A kind of hot press-formed ultra-thin hot-rolled strip steel and its production method |
| CN109628846A (en) * | 2018-12-20 | 2019-04-16 | 唐山钢铁集团有限责任公司 | 1300MPa grades of automobile super high tensile cold-rolled steel plates and its production method |
| CN109628846B (en) * | 2018-12-20 | 2020-08-04 | 唐山钢铁集团有限责任公司 | 1300 MPa-grade ultrahigh-strength cold-rolled steel plate for automobiles and production method thereof |
| CN110129670A (en) * | 2019-04-25 | 2019-08-16 | 首钢集团有限公司 | A kind of 1300MPa grades of High-strength high-plasticity drop stamping steel and preparation method thereof |
| CN110257702A (en) * | 2019-06-24 | 2019-09-20 | 鞍钢股份有限公司 | Steel for hot stamping forming and hot forming method thereof |
| CN111321341A (en) * | 2019-12-03 | 2020-06-23 | 马鞍山钢铁股份有限公司 | 1500 MPa-grade non-coating hot forming steel with low high-temperature friction coefficient and preparation method thereof |
| CN113528932A (en) * | 2021-05-31 | 2021-10-22 | 唐山钢铁集团高强汽车板有限公司 | Martensite steel plate and preparation method thereof |
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