CN101649412A - Hadifield steel with excellent mechanical property and manufacturing method thereof - Google Patents
Hadifield steel with excellent mechanical property and manufacturing method thereof Download PDFInfo
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- CN101649412A CN101649412A CN200810041728A CN200810041728A CN101649412A CN 101649412 A CN101649412 A CN 101649412A CN 200810041728 A CN200810041728 A CN 200810041728A CN 200810041728 A CN200810041728 A CN 200810041728A CN 101649412 A CN101649412 A CN 101649412A
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Abstract
The invention provides hadifield steel with excellent mechanical property, which comprises the following chemical components in percentage by weight: 0.3 to 1.0 percent of C, 15.0 to 30.0 percent of Mn, less than or equal to 0.025 percent of P, less than or equal to 0.025 percent of S, 0.1 to 0.4 percent of V or 0.02 to 0.06 percent of Ti, and the balance of Fe and inevitable impurities. The invention also provides a method for manufacturing the steel, which comprises the processes of pouring, casting, hot rolling, cooling and reeling. Without Ai and Si elements, the hadifield steel has good TWIP effect, high strength and high plasticity, which can be used for manufacturing automobile components with high strength, high plasticity and high impact absorption energy.
Description
Technical field
The present invention relates to a kind of steel, specifically, the present invention relates to have the high mangaenese steel of good mechanical property.
Background technology
At present, developing of automobile industry trend is loss of weight, energy-conservation, raising security, and high-strength steel can satisfy the requirement of loss of weight and raising security simultaneously, thereby, high-strength steel is used one of development trend of steel as Hyundai Motor, just more and more be subjected to the attention of automobile factory and Steel Plant.Through years of development, to use the intensity of high tensile steel plate be 340～1470MPa to automobile industry at present, the ratio that high tensile steel plate accounts for the whole steel plate total amounts of automobile from 1979 8.2% develop into more than 30% in 2000, and the trend of further rising is arranged.
Area under the stress-strain curve of steel when stretching has characterized the size of the mechanical energy that the material deformation process consumed, the numerical value of this area has reflected the preceding endergonic size of material damage, and the product of the tensile strength of material and unit elongation absorbs the ability of clashing into energy before having reflected material damage to a certain extent.For high-strength steel, the raising of plasticity not only can increase its processability, and its bump absorbs and can also obviously improve.Mould by force (tensile strength and the unit elongation) of high Strength Steel for Motor Vehicles amasss all below 25000MPa% at present.In addition, the another one problem of high-strength steel is delayed fracture, and generally along with the increase of intensity, the resistance for delayed fracture variation of steel is the resistance for delayed fracture main reasons for decrease that causes steel and inhale hydrogen.
But, intensity and plasticity are a pair of contradiction of steel performance aspect, and generally along with the lifting of intensity, plasticity can descend, this has not only reduced the formability of material, and the important indicator (product of intensity and unit elongation) of measurement bump absorption energy can not be improved significantly.Therefore, obtain certain breakthrough on intensity and plasticity over-all properties is the target that the professional person pursued always, is a kind of approach that improves plasticity effectively and utilize TWIP (Twinning Induced Plasticity) effect.
Although the use of high mangaenese steel is with a long history, it is mainly used in makes anti impact wear-proof, nonmagnetic or parts of stainless steel, and the application facet at high-strength steel does not obtain paying attention to.By retrieval, the patent documentation of finding relevant high mangaenese steel is substantially all about high-abrasive material, non-magnetic steel, lower temperature application and high mangaenese steel casting or welding aspect, as the patent of invention of high tensile steel plate aspect seldom.
Patent documentation US5,431,753A discloses a kind of high tensile steel plate of producing with high mangaenese steel, its main component is (weight): C:＜1.5%, Mn:15.0～35.0%, Al:2.0～6.0%, adding one or more is selected from by less than 0.6% Si, Cu less than 5.0%, Nb less than 1.0%, V less than 0.5%, Ti less than 0.5%, Cr less than 9.0%, Ni less than 4.0% reaches less than the element in 0.2% the group that N constituted, and emphasis done certain restriction to the interpolation of Mn and Al, emphasized that Mn and Al element are to the alloy Effect on Performance.The steel of this composition can be produced hot-rolled steel sheet or cold-reduced sheet through controlled rolling and controlled cooling.
Patent documentation DE102005062221 discloses a kind of composition and method of producing high tensile steel plate with high mangaenese steel.The main component of described high mangaenese steel is (weight): C:0.05～1.0%, Mn:9.0～25.0%, and Al:0.1～11.0%, Si:0～6.0%, surplus is Fe and unavoidable impurities element.Emphasis has been done restriction to the adding proportion relation of Mn and C, so that utilize the TRIP effect to obtain better mechanical property.
Patent documentation CN200480044461.3 discloses hot-rolled high-strength steel plate band or the steel-sheet method that a kind of production has the TWIP effect.Described steel plate has following main component (weight): C:0.003～1.5%, Mn:18.0～30.0%, Ni :≤10%, Al :≤10%, Si :≤8%, N :≤0.06%, Cr :≤10%, Cu :≤3%, P :≤0.4%, S :≤0.15%, surplus is Fe and unavoidable impurities element.The alloy that will have these compositions is finished hot rolling by controlled rolling and controlled cooling more than 700 ℃, batches in the temperature below 750 ℃.
Patent documentation CN200680007190.3 discloses a kind of composition and production unit of high manganese lightweight structural steel.The main component of described high mangaenese steel is (weight): C:＜0.8%, and Mn:15.0～27.0%, Al:1.0～6.0%, Si:1.0～6.0%, surplus is Fe and unavoidable impurities element.The alloy that will have these compositions is realized temperature equilibrium by a kind of thin slab casting machine casting in intermediate furnace, without intercooling and directly hot rolling, thereby solidified shell intensity is low when having solved the high mangaenese steel continuous casting, occurs drawing crack easily, the problem of bleed-out.
The main component of steel sees Table 1 in the above-mentioned relevant patent documentation.
The main component (wt%) of steel in the relevant patent documentation of table 1:
| Patent document number | ??C | ??Si | ??Mn | ??Al | ??Ti | ?V |
| ??US5,431,753 | ??＜1.5 | ??＜0.6 | ??15.0～35.0 | ??2.0～6.0 | ??＜0.5 | ?＜0.5 |
| ??DE102005062221 | ??0.05～1.0 | ??＜6.0 | ??9.0～25.0 | ??0.1～11.0 | ??/ | ?/ |
| ??CN200480044461.3 | ??0.003～1.5 | ??＜8.0 | ??18.0～30.0 | ??＜10.0 | ??/ | ?/ |
| ??CN200680007190.3 | ??＜0.8 | ??1.0～6.0 | ??12.0～27.0 | ??1.0～6.0 | ??/ | ?/ |
As can be seen from Table 1, all added a large amount of Al and Si element in the disclosed high mangaenese steel of above-mentioned patent documentation, this has not only increased the cost of alloy, and the Al element easily forms Al when casting
2O
3, stop up the mouth of a river, cause the casting difficulty; Si then is one of the element that has a strong impact on the platability of alloy, can not satisfy the surface requirements of automobile steel.
For addressing the above problem, order of the present invention is to provide a kind of does not add Al and Si element, have the high mangaenese steel and the manufacture method thereof of the high-strength high-plasticity of TWIP effect preferably.
Summary of the invention
The invention provides a kind of high mangaenese steel with good mechanical property, by weight percentage, its chemical ingredients comprises: C:0.3～1.0%, Mn:15.0～30.0%, V:0.1～0.4% or Ti:0.02～0.06%, P :≤0.025%, S :≤0.025%, all the other are Fe and unavoidable impurities.
Wherein, the weight percentage of described C preferred 0.5～0.9%; The weight percentage of described P preferably≤0.01%; The weight percentage of described S preferably≤0.006%; Preferred 31≤15 * C of the relation of described Mn and described C (wt%)+Mn (wt%)≤36.
The reasons are as follows of alloy designs of the present invention:
C:C is important solution strengthening element, is the assurance that obtains high-strength steel.If C content is low excessively, the effect of solution strengthening can not get maximum performance, is difficult to guarantee the high strength of material requirements; If the C too high levels, carbide precipitate on crystal boundary easily reduces the plasticity of material.Therefore, the content range of C is advisable with 0.3～1.0%, and preferred 0.5～0.9%.
The main effect of Mn:Mn is to be used for replacing Ni with stable austenite, and steel is when distortion, and stable austenite can produce a large amount of tiny twins, increases substantially the plasticity of steel, reduces the production cost of steel simultaneously.Experiment showed, that if Mn content is low excessively then the austenite instability in the steel in processing or use, thereby may produce the plasticity that more martensite reduces steel; If the Mn too high levels, not only can increase the cost of steel, and the intensity of steel and plasticity can reduce all.Therefore, the content range of Mn is advisable with 15.0～30.0%.
V: steel can be separated out carbide or the carboritride of V when take-up, but the carbide of V is a kind of effectively trap of diffustivity hydrogen, make the hydrogen uniform distribution that enters, purify the absorption hydrogen of crystal boundary, can obviously improve owing to inhale hydrogen embrittlement or the delay cracking performance that hydrogen causes.Therefore, the content range of V is advisable with 0.1～0.40%.
The effect of Ti:Ti is similar to V, can form carbide or the carboritride of Ti, can obviously improve owing to inhale hydrogen embrittlement or the delay cracking performance that hydrogen causes.But the Ti constituent content is unsuitable too high, and too high meeting causes carbide or carbonitride to grow up, and reduces the plasticity of material.Therefore, the content range of Ti is advisable with 0.02～0.06%.
P: owing to contain a large amount of Mn elements in the steel, can increase P poly-partially at crystal boundary, the crystal boundary that weakens is so P content should reduce as far as possible.Therefore, the content range of P is advisable with≤0.025%, preferred≤0.01%.
S: owing to contain a large amount of Mn elements in the steel, S easily forms MnS in steel, cause hot-short, so S content is few more good more.Therefore, the content range of S is advisable with≤0.025%, preferred≤0.006%.
The relation of Mn and C: 31≤15 * C (wt%)+Mn (wt%)≤36.Because the content of Mn and C is all influential to austenitic stability and stacking fault energy in the steel, when if Mn and C content are all near the lower limit of composition range, thereby steel produces martensite easily in processing or use makes plasticity reduce the high-ductility that a large amount of twins bring when having lost stable austenite deformation; When Mn and C content were all near the upper limit of composition range, the intensity of steel and the overall advantage of plasticity were not obvious, have increased the cost and the manufacture difficulty of steel on the contrary.The synoptic diagram of Mn and C relation with contents is seen Fig. 1.
The present invention also provides the manufacture method of described high mangaenese steel, comprise cast, casting, hot rolling, cooling, coiling process, described high mangaenese steel its chemical ingredients by weight percentage comprises: C:0.3～1.0%, Mn:15.0～30.0%, V:0.1～0.4% or Ti:0.02～0.06%, P :≤0.025%, S :≤0.025%, all the other are Fe and unavoidable impurities.Wherein, teeming temperature can be 1450～1490 ℃ in the described cast operation; Described casting process can adopt die casting or continuous casting; Rolling temperature can be 1180～1250 ℃ in the described hot-rolled process, and finishing temperature can be 870～930 ℃; Described refrigerating work procedure can adopt air cooling 3～5 seconds, then water-cooled; Coiling temperature can be 500～560 ℃ in the described coiling process.
Wherein, also can comprise pickling, cold rolling, annealing operation behind the described hot-rolled process.Cold rolling draft can be 40%～80% in the described cold rolling process; Described annealing operation can adopt continuous annealing or cover annealing, and annealing temperature can be 500～950 ℃, and annealing time can be 2～360min.After the annealing of differing temps, the grain-size of this steel is about 1～40um, and the yield strength of steel is about 300～650MPa, therefore, can yield strength as required select different annealing temperatures.
The mechanical property of hot-rolled steel is: Rp0.2=450～550MPa, Rm 〉=900MPa, A50 〉=50%, Rm * A50 〉=50000MPa%.
The mechanical property of cold-rolled steel is: Rp0.2=300～650MPa, Rm 〉=900MPa, A50 〉=50%, Rm * A50 〉=50000MPa%.
Beneficial effect of the present invention is:
Steel of the present invention has high strength and high-ductility, can satisfy automotive industry loss of weight, energy-conservation, the development trend that improves security well, can be used for making high strength on the automobile, high-ductility and high bump absorb can parts.
Description of drawings
Fig. 1 represents the relation with contents of Mn and C in the steel of the present invention.
Fig. 2 represents the metallographic structure after the steel hot rolling of the present invention.
Embodiment
Below for a more detailed description with embodiment to the present invention.These embodiment only are the descriptions to best mode for carrying out the invention, scope of the present invention are not had any restriction.
Embodiment 1～10
The embodiment of table 2 expression steel of the present invention and the chemical ingredients of comparative example, wherein A1～A10 represents the embodiment of the invention respectively, and B1～B4, C1～C4 represent comparative example respectively, is respectively patent documentation US5,431, the steel among 753A and the patent documentation CN200480044461.3.Table 3 has been listed the mechanical property of the embodiment of the invention and comparative example.
The chemical ingredients of table 2 embodiment and comparative example, wt%
The mechanical property of table 3 steel of the present invention and comparative steel
Continuous table 3
Claims (13)
1, a kind of high mangaenese steel is characterized in that comprising the chemical ingredients of following weight percent: C:0.3～1.0%, Mn:15.0～30.0%, V:0.1～0.4% or Ti:0.02～0.06%, P :≤0.025%, S :≤0.025%, all the other are Fe and unavoidable impurities.
2, high mangaenese steel as claimed in claim 1 is characterized in that, the weight percentage of described C is 0.5～0.9%.
3, high mangaenese steel as claimed in claim 1 is characterized in that, the weight percentage of described P≤0.01%.
4, high mangaenese steel as claimed in claim 1 is characterized in that, the weight percentage of described S≤0.006%.
5, high mangaenese steel as claimed in claim 1 is characterized in that, the pass of described Mn and described C is: 31≤15 * C (wt%)+Mn (wt%)≤36.
6, the manufacture method of the described high mangaenese steel of claim 1, comprise cast, casting, hot rolling, cooling, coiling process, it is characterized in that, described high mangaenese steel comprises the chemical ingredients of following weight percent: C:0.3～1.0%, Mn:15.0～30.0%, V:0.1～0.4% or Ti:0.02～0.06%, P :≤0.025%, S :≤0.025%, all the other are Fe and unavoidable impurities.
7, manufacture method as claimed in claim 6 is characterized in that, teeming temperature is 1450～1490 ℃ in the described cast operation.
8, manufacture method as claimed in claim 6 is characterized in that, described casting process adopts die casting or continuous casting.
9, manufacture method as claimed in claim 6 is characterized in that, rolling temperature is 1150～1250 ℃ in the described hot-rolled process, and finishing temperature is 870～930 ℃.
10, manufacture method as claimed in claim 6 is characterized in that, described refrigerating work procedure is air cooling 3～5 seconds, water-cooled then.
11, manufacture method as claimed in claim 6 is characterized in that, coiling temperature is 500～560 ℃ in the described coiling process.
12, manufacture method as claimed in claim 6 is characterized in that, also comprises pickling, cold rolling, annealing operation behind the described hot-rolled process, and cold rolling draft is 40%～80% in the described cold rolling process.
13, manufacture method as claimed in claim 6 is characterized in that, also comprises pickling, cold rolling, annealing operation behind the described hot-rolled process, and described annealing operation is continuous annealing or cover annealing, and annealing temperature is 500～950 ℃, and annealing time is 2～360min.
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Cited By (10)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102199732A (en) * | 2010-03-25 | 2011-09-28 | 宝山钢铁股份有限公司 | Boron containing steel plate for heat treatment and manufacturing method thereof |
| CN102418032A (en) * | 2011-12-09 | 2012-04-18 | 北京科技大学 | Annealing preparation process for enhancing product of strength and elongation of twinning-induced plasticity high-manganese steel board |
| CN102423795A (en) * | 2011-11-25 | 2012-04-25 | 山西太钢不锈钢股份有限公司 | Continuous casting method for high manganese steel |
| CN107574376A (en) * | 2017-09-07 | 2018-01-12 | 北京科技大学 | A kind of high manganese TWIP/TRIP effects symbiosis steel of high strength and low cost plastotype and preparation method thereof |
| CN107760997A (en) * | 2017-09-25 | 2018-03-06 | 武汉钢铁有限公司 | Dual induced plastic high-strength steel and its manufacture method |
| CN108315655A (en) * | 2018-05-14 | 2018-07-24 | 东北大学 | A kind of high-yield strength LNG storage tank high manganese cut deal and preparation method thereof |
| CN109518098A (en) * | 2018-10-29 | 2019-03-26 | 南京钢铁股份有限公司 | A kind of austenitic cryogenic steel and preparation method thereof |
| US20190292616A1 (en) * | 2016-05-24 | 2019-09-26 | Arcelormittal | Twip steel sheet having an austenitic matrix |
| CN112662931A (en) * | 2019-10-15 | 2021-04-16 | 中国石油化工股份有限公司 | Method for simultaneously improving strength and plasticity of austenitic steel and product thereof |
| CN112877612A (en) * | 2021-01-07 | 2021-06-01 | 浙江工业大学 | Preparation method of high-manganese TWIP steel |
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2008
- 2008-08-15 CN CN200810041728A patent/CN101649412A/en active Pending
Cited By (12)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102199732A (en) * | 2010-03-25 | 2011-09-28 | 宝山钢铁股份有限公司 | Boron containing steel plate for heat treatment and manufacturing method thereof |
| CN102199732B (en) * | 2010-03-25 | 2013-04-24 | 宝山钢铁股份有限公司 | Boron containing steel plate for heat treatment and manufacturing method thereof |
| CN102423795A (en) * | 2011-11-25 | 2012-04-25 | 山西太钢不锈钢股份有限公司 | Continuous casting method for high manganese steel |
| CN102423795B (en) * | 2011-11-25 | 2013-08-28 | 山西太钢不锈钢股份有限公司 | Continuous casting method for high manganese steel |
| CN102418032A (en) * | 2011-12-09 | 2012-04-18 | 北京科技大学 | Annealing preparation process for enhancing product of strength and elongation of twinning-induced plasticity high-manganese steel board |
| US20190292616A1 (en) * | 2016-05-24 | 2019-09-26 | Arcelormittal | Twip steel sheet having an austenitic matrix |
| CN107574376A (en) * | 2017-09-07 | 2018-01-12 | 北京科技大学 | A kind of high manganese TWIP/TRIP effects symbiosis steel of high strength and low cost plastotype and preparation method thereof |
| CN107760997A (en) * | 2017-09-25 | 2018-03-06 | 武汉钢铁有限公司 | Dual induced plastic high-strength steel and its manufacture method |
| CN108315655A (en) * | 2018-05-14 | 2018-07-24 | 东北大学 | A kind of high-yield strength LNG storage tank high manganese cut deal and preparation method thereof |
| CN109518098A (en) * | 2018-10-29 | 2019-03-26 | 南京钢铁股份有限公司 | A kind of austenitic cryogenic steel and preparation method thereof |
| CN112662931A (en) * | 2019-10-15 | 2021-04-16 | 中国石油化工股份有限公司 | Method for simultaneously improving strength and plasticity of austenitic steel and product thereof |
| CN112877612A (en) * | 2021-01-07 | 2021-06-01 | 浙江工业大学 | Preparation method of high-manganese TWIP steel |
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Open date: 20100217 |