CN1325686C - Process for producing super high carbon steel - Google Patents
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- CN1325686C CN1325686C CNB2004100255191A CN200410025519A CN1325686C CN 1325686 C CN1325686 C CN 1325686C CN B2004100255191 A CNB2004100255191 A CN B2004100255191A CN 200410025519 A CN200410025519 A CN 200410025519A CN 1325686 C CN1325686 C CN 1325686C
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- 238000000034 method Methods 0.000 title claims abstract description 24
- 229910000677 High-carbon steel Inorganic materials 0.000 title abstract 6
- 238000004519 manufacturing process Methods 0.000 claims abstract description 26
- 238000005516 engineering process Methods 0.000 claims abstract description 16
- 238000005096 rolling process Methods 0.000 claims abstract description 12
- 238000010438 heat treatment Methods 0.000 claims abstract description 11
- 239000000956 alloy Substances 0.000 claims abstract description 10
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 5
- 239000000203 mixture Substances 0.000 claims abstract description 5
- 238000005098 hot rolling Methods 0.000 claims description 32
- 229910000975 Carbon steel Inorganic materials 0.000 claims description 31
- 239000010962 carbon steel Substances 0.000 claims description 30
- 238000010107 reaction injection moulding Methods 0.000 claims description 18
- 238000012545 processing Methods 0.000 claims description 14
- 238000005275 alloying Methods 0.000 claims description 12
- 239000000470 constituent Substances 0.000 claims description 12
- 238000009718 spray deposition Methods 0.000 claims description 9
- 238000007669 thermal treatment Methods 0.000 claims description 9
- 238000001816 cooling Methods 0.000 claims description 7
- 238000009413 insulation Methods 0.000 claims description 7
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 claims description 6
- 239000000758 substrate Substances 0.000 claims description 4
- 238000013461 design Methods 0.000 claims description 3
- 230000006698 induction Effects 0.000 claims description 3
- 229910052757 nitrogen Inorganic materials 0.000 claims description 3
- 239000002994 raw material Substances 0.000 claims description 2
- 238000002791 soaking Methods 0.000 claims description 2
- 244000218514 Opuntia robusta Species 0.000 claims 1
- 238000005265 energy consumption Methods 0.000 abstract description 3
- 229910000831 Steel Inorganic materials 0.000 abstract 1
- 230000002349 favourable effect Effects 0.000 abstract 1
- 238000000465 moulding Methods 0.000 abstract 1
- 229910001562 pearlite Inorganic materials 0.000 abstract 1
- 239000010959 steel Substances 0.000 abstract 1
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical group [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 11
- 239000000463 material Substances 0.000 description 11
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 4
- 229910052799 carbon Inorganic materials 0.000 description 4
- 238000005242 forging Methods 0.000 description 4
- 230000008520 organization Effects 0.000 description 4
- 235000019362 perlite Nutrition 0.000 description 4
- 239000010451 perlite Substances 0.000 description 4
- 238000004458 analytical method Methods 0.000 description 3
- 238000005266 casting Methods 0.000 description 3
- 238000001192 hot extrusion Methods 0.000 description 3
- 239000000126 substance Substances 0.000 description 3
- 230000009286 beneficial effect Effects 0.000 description 2
- 239000007789 gas Substances 0.000 description 2
- 238000010275 isothermal forging Methods 0.000 description 2
- 239000003607 modifier Substances 0.000 description 2
- 238000002360 preparation method Methods 0.000 description 2
- 239000000243 solution Substances 0.000 description 2
- 238000005507 spraying Methods 0.000 description 2
- 238000003723 Smelting Methods 0.000 description 1
- 229910001566 austenite Inorganic materials 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 238000010276 construction Methods 0.000 description 1
- 238000005336 cracking Methods 0.000 description 1
- 230000002950 deficient Effects 0.000 description 1
- 238000011161 development Methods 0.000 description 1
- 239000006185 dispersion Substances 0.000 description 1
- 239000010419 fine particle Substances 0.000 description 1
- 239000007788 liquid Substances 0.000 description 1
- 239000011159 matrix material Substances 0.000 description 1
- 238000005457 optimization Methods 0.000 description 1
- 230000002265 prevention Effects 0.000 description 1
- 238000011160 research Methods 0.000 description 1
- 238000005204 segregation Methods 0.000 description 1
- 238000009827 uniform distribution Methods 0.000 description 1
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Abstract
The present invention relates to a process for producing super high carbon steel. The super high carbon steel has the alloy compositions of (wt%) 1.0 to 1.8% of C, 0.5 to 3.0% of Si, 0.5 to 2.0% of Cr, 0.2 to 0.7% of Mn, and Fe as the rest. The deformation and heat treatment combining production technology applied to the super high carbon steel produced by jet molding has the steps that the jet forming super high carbon steel is maintained in a furnace for 20 minutes at 1000 DEG C before taking out for rolling in a one-pass roller mode and the rolling reduction is 60 %, and the rolled steel is quickly placed into a heat treatment furnace which already reaches to the given temperature and is maintained for 150 minutes before taken out. The super high carbon steel obtained by the combined production process has a special organizational structure combined by pearlite and nodulized structure in a proper ratio, the tensile strength can reach to 1300MPa, and the specific elongation is 18.5%. The present invention has the advantages of simple manufacturing process, and obvious reduced energy consumption and production cost; the present invention is favorable for the realization of scale production, and popularization and application.
Description
Technical field
The present invention relates to a kind of production technique of superhigh carbon steel.
Background technology
(carbon content 1.0～2.1wt%) adopts conventional smelting casting process preparation because carbon content is very high to superhigh carbon steel, is difficult to avoid the segregation of carbon and the formation of thick carbide; Because carbon content far surpasses eutectoid composition, in conventional hot procedure, also be difficult to avoid form on the austenite grain boundary thick carbide network again.These defectives all can cause the fatal fragility of material, thereby it can't actually be used.Therefore, can obtain practical application as the superhigh carbon steel of iron structure material, key is to improve its obdurability.
Preparing the serious problems that exist at superhigh carbon steel, is that a collection of metallurgist of representative has proposed a series of quite complicated hot mechanical technology routes with Sherby.They find that superhigh carbon steel can make and organize abundant refinement and homogenizing through behind the hot mechanical treatment of multiple working procedure, and have high strength and certain toughness plasticity matches, and also have good superplasticity simultaneously.
The research of the relevant superhigh carbon steel of Sherby has obtained multinomial patent, and the mentioned technology of these patents mainly comprises two portions: the first, eliminate the appearance of thick carbide and prevention grain boundary carbide network by the processing of multi-pass elevated temperature heat; The second, the thermal treatment of employing several different methods or temperature processing or both combining make carbide be distributed in matrix with fine particle form even dispersion.On this basis, the hot extrusion technique route that Sherby is made up of three parts in proposition in 1999 again (publish in " Metallurgical And Materials Transaction ", Vol.30A, 1999, p1559.):
The first, vacuum-casting;
The second, in two steps ingot casting is carried out high temperature-middle warm forging and make: step 1: rise and forge 1100 ℃, 900 ℃ of finish-forgings;
Step 2: rise and forge 900 ℃, 700 ℃ of finish-forgings;
The 3rd, under 900 ℃ or 1025 ℃ or 1150 ℃, carry out hot extrusion.
Above-mentioned hot extrusion technique and since need two steps high, middle warm forging is made and the large-tonnage heat extruder, energy consumption increases and cost is higher and technology too problem such as complexity still fail solution.
In view of this, the superhigh carbon steel preparation technology that Sherby proposes utilizes the existing means of production, is difficult to realize scale production and applies.
Chinese patent application number 02136305.6 discloses with reaction-injection moulding produces blank, then it is implemented isothermal forging, need not modifier treatment behind the air cooling can obtain yield strength and reach～900MPa, tensile strength reaches～1200MPa, and unit elongation reaches～10% superhigh carbon steel material.
Chinese patent application number 02150879.8 discloses chooses suitable interpolation element, produce the superhigh carbon steel blank with spray deposition processing, then it is carried out aximal deformation value (draught reaches 50%～70%) hot rolling, the gained material need not modifier treatment behind the air cooling, can reach tensile strength about 1300MPa and 8～11% unit elongation.
Above-mentioned two kinds of technologies are done one relatively: technology one needs to use isothermal forging equipment, and cost is higher and productivity is lower, thereby will be restricted on range of application and industrial scale; The characteristics of technology two are, not only can utilize the common hot rolling means of production that the reaction-injection moulding blank is carried out deformation processing, and the performance of gained material also is better than technology one material, and process implementing is very convenient again simultaneously.
Summary of the invention
In view of the problems such as the big cost height of energy consumption that exist in the present superhigh carbon steel development, the object of the present invention is to provide a kind of production technique of superhigh carbon steel, the over-all properties that reaction-injection moulding superhigh carbon steel acquisition high strength and good plasticity are matched; And, implement this technology, not only operation is easy, and production cost and energy expenditure all can reduce, thereby helps realizing scale production and apply.
Technical solution of the present invention is a kind of production technique of superhigh carbon steel:
A) alloying constituent (weight percent)
C 1.0～1.8；
Si 0.5～3.5；
Cr 0.5～2.0；
Mn 0.2～0.7；
Surplus Fe.
B) spray deposition processing is produced blank, to provide the mother alloy of alloying constituent as raw material, the employing spray deposition processing is produced, the mother alloy material is put into induction furnace internal heating fusing, keep for some time being higher than under 150～250 ℃ of temperature of fusing point, make the temperature of liquation and composition reach even, with high pressure nitrogen to spraying by the effusive melt of catheter, making it atomizing becomes fine drop, flies and is deposited on and collect on the substrate, finishes to solidify and form heat supply and rolls and use the blank block; This block superhigh carbon steel is owing to have a good original structure, and it has the high temperature deformation ability of the excellence that general alloy material do not have, and therefore can implement the hot-work of aximal deformation value to it;
C) the reaction-injection moulding blank carries out hot rolling, hot-rolled temperature: 950 ℃～1100 ℃, and single pass hot rolling draught: 50%～70%; Because material has the excellent high-temperature deformability, in the hot-rolled temperature scope that provides, can realize the hot rolling processing of a time aximal deformation value (draught is up to 70%) and do not ftracture;
D) plate is heat-treated after the hot rolling, plate after the hot rolling is put into the heat treatment furnace insulation that has reached design temperature immediately take out air cooling after 112～187 minutes, and the heat treatment furnace temperature is set: 700 ℃～850 ℃; Preferred temperature: 700 ℃～800 ℃, heat treated enforcement makes the plate after rolling obtain to have the perlite of proper ratio and the particular tissues structure that spherodized structure matches.
Wherein, the alloying constituent of mother alloy (weight percent) is preferably:
C 1.2～1.5；
Si 2.0～3.0；
Cr 1.0～2.0；
Mn 0.2～0.7；
Surplus Fe.
The preferred hot-rolled temperature of described hot rolling: 1000 ℃, preferred draught is 60%.
Before rolling blank is put into the process furnace that reaches preset temperature and be incubated, soaking time determines that according to sotck thinkness promptly the corresponding 0.75mm of per minute takes out after the insulation and carries out the single pass heavy reduction rolling immediately.
Beneficial effect of the present invention
Select suitable superhigh carbon steel alloying constituent for use, adopt spray deposition processing to produce blank, then the gained blank is implemented by hot rolling and heat treatment phase bonded combined production process, thus obtained material reaches advanced world standards its over-all properties because of the optimum combination of perlite with proper ratio and spherodized structure.
Adopt the operational path of Sherby, mainly can obtain two kinds of superhigh carbon steels.A kind of is spherodized structure, and another kind is a pearlitic structure.The superhigh carbon steel of single pearlitic structure, though intensity is very high, plasticity is very poor.Tensile strength can reach 1700MPa, but unit elongation only drops to 2.8%.And the superhigh carbon steel with spherodized structure, although plasticity obviously increases, intensity is undesirable.Unit elongation can reach 28%, but tensile strength drops to only 880MPa.
Different with the operational path of above-mentioned Sherby, a kind of combined production process of optimizing the superhigh carbon steel over-all properties that the present invention proposes, can obtain to have the superhigh carbon steel of particular tissues structure, can bring into play pearlitic strength advantage, can make full use of again spherodized structure make its toughness plasticity be improved significantly.By the material that production technique of the present invention obtains, tensile strength can reach 1300MPa, and unit elongation is 18.5%.Compare (tensile strength: 1048MPa with the top performance level that the superhigh carbon steel of Sherby can reach; Unit elongation: 20.7%), unit elongation is suitable, and the intensity decided advantage.What be worth emphasizing is, production technique provided by the invention is simplified more than the hot mechanical technology of the complexity of Sherby and effectively.
Description of drawings
Fig. 1 is the organization chart of reaction-injection moulding blank of the present invention.
Organization chart after reaction-injection moulding blank process hot rolling shown in Figure 2 and thermal treatment combined production process are handled.
Embodiment
Embodiment 1
(1) alloying constituent (chemical analysis results, weight %): the surplus Fe of 1.17C-2.87Si-0.50Mn-1.58Cr-;
(2) reaction-injection moulding is produced blank
The mother alloy material is put into crucible induction furnace melt, the liquation superheating temperature is about 150 ℃; The catheter internal diameter is φ 4mm; Atomizing gas (nitrogen) pressure is 2.2MPa, and spraying gun is about 360mm to distance between the collector substrate, and the substrate speed of rotation is 10rpm; Gas/liquid inventory is about 0.30M than (G/M)
3/ kg.Adopt above-mentioned processing parameter to produce the reaction-injection moulding blank, this block superhigh carbon steel blank makes its high temperature deformation ability that has the excellence that general alloy material do not have owing to having good original structure (as shown in Figure 1), therefore can implement the hot-work of aximal deformation value to it;
(3) reaction-injection moulding blank hot rolling
Cut the bar shaped blank of thick 15mm from the reaction-injection moulding blank, sample one end is processed into wedge shape, is convenient to nip when rolling.Blank is put into the insulation of 1000 ℃ of stoves and is taken out after 20 minutes that to send into maximum rolling force immediately be that the hot rolls of 3000KN is rolled, and it is thick that single pass is rolling to 6mm with blank, and draught is 60%.Rolling back plate is not found cracking phenomena.
(4) rolling back plate thermal treatment
Rolling back plate is put into temperature immediately and is set to 700 ℃ heat treatment furnace insulation and promptly takes out air cooling after 150 minutes.
Embodiment 2
(1) alloying constituent
With embodiment 1;
(2) spray deposition processing is produced blank
With embodiment 1;
(3) reaction-injection moulding blank hot rolling
Hot rolling technology is with embodiment 1;
(4) plate thermal treatment after the hot rolling
Plate is put into temperature immediately and is set at 750 ℃ heat treatment furnace insulation and promptly takes out air cooling after 150 minutes after the hot rolling.
Embodiment 3
(1) alloying constituent (chemical analysis results, weight %): the surplus Fe of 1.17C-1.91Si-0.50Mn-1.56Cr-;
(2) spray deposition processing is produced blank
With embodiment 1;
(3) reaction-injection moulding blank hot rolling
Hot rolling technology is with embodiment 1;
(4) plate thermal treatment after the hot rolling
Plate is put into temperature immediately and is set to 800 ℃ heat treatment furnace insulation and promptly takes out air cooling after 150 minutes after the hot rolling.
Embodiment 4
(1) alloying constituent (chemical analysis results, weight %): the surplus Fe of 1.50C-2.0Si-0.50Mn-1.57Cr-;
(2) spray deposition processing is produced blank
With embodiment 1;
(3) reaction-injection moulding blank hot rolling
Hot rolling technology is with embodiment 1;
(4) plate thermal treatment after the hot rolling
With embodiment 1.
Embodiment 5
(1) alloying constituent
With embodiment 4.
(2) spray deposition processing is produced blank
With embodiment 1.
(3) reaction-injection moulding blank hot rolling
With embodiment 3.
(4) plate thermal treatment after the hot rolling
With embodiment 3.
The superhigh carbon steel that the foregoing description is produced has excellent comprehensive performances, is shown in Table 1.
Table 1
| Composition (weight percent) | Yield strength (Mpa) | Tensile strength (MPa) | Unit elongation (%) | |
| Embodiment 1 | 1.17C-2.87Si-0.50Mn-1.58Cr-surplus Fe | 924 | 1198 | 18.5 |
| Embodiment 2 | 1.17C-2.87Si-0.50Mn-1.58Cr-surplus Fe | 867 | 1099 | 20.5 |
| Embodiment 3 | 1.17C-1.91Si-0.50Mn-1.56Cr-surplus Fe | 863 | 1300 | 18.5 |
| Embodiment 4 | 1.17C-1.91Si-0.50Mn-1.56Cr-surplus Fe | 861 | 1109 | 17.5 |
| Embodiment 5 | 1.50C-2.00Si-0.50Mn-1.57Cr-surplus Fe | 846 | 1189 | 16.5 |
Fig. 1 is the organization chart of reaction-injection moulding blank of the present invention.As can be seen from the figure, the carbides-free network has evenly fine and closely woven pearlitic structure.
Organization chart after reaction-injection moulding blank process hot rolling shown in Figure 2 and thermal treatment combined production process are handled.As scheme to show, around the perlite uniform distribution some amount be similar to the globular carbide.The optimization weave construction that this perlite with proper ratio matches with spherodized structure is very beneficial for the raising of material over-all properties.
Claims (6)
1. the production technique of a superhigh carbon steel is characterized in that, comprises the steps:
The alloying constituent weight percent of the superhigh carbon steel of a. selecting for use is:
C 1.0～1.8；
Si 0.5～3.5；
Cr 0.5～2.0；
Mn 0.2～0.7；
Surplus Fe;
B. with the mother alloy of above-mentioned alloying constituent as raw material, adopt spray deposition processing, the mother alloy material is put into the fusing of induction furnace internal heating, keep for some time being higher than under 150 ℃～250 ℃ temperature of fusing point, the temperature and the composition of liquation are reached evenly, and to being sprayed by the effusive melt of catheter, making it atomizing becomes fine drop with high pressure nitrogen, flight also is deposited on collects on the substrate, finishes to solidify and form heat supply and rolls and use the blank block;
C. the reaction-injection moulding blank is carried out hot rolling; Hot-rolled temperature: 950 ℃～1110 ℃, hot rolling draught: 50%～70%;
D. plate after the hot rolling is heat-treated: plate puts into immediately that to have reached design temperature be 700 ℃～850 ℃ heat treatment furnace insulation 112～187 minutes after the hot rolling, takes out air cooling then.
2. the production technique of superhigh carbon steel as claimed in claim 1 is characterized in that, the alloying constituent weight percent of described mother alloy is:
C 1.2～1.5；
Si 2.0～3.0；
Cr 1.0～2.0；
Mn 0.2～0.7；
Surplus Fe.
3. the production technique of superhigh carbon steel as claimed in claim 1 is characterized in that, the hot-rolled temperature of described hot rolling technology is that 1000 ℃, draught are 60%.
4. the production technique of superhigh carbon steel as claimed in claim 1 is characterized in that, described hot rolling adopts that a time is rolling finishes predetermined draught.
5。The production technique of superhigh carbon steel as claimed in claim 1 is characterized in that, described thermal treatment process temperature: 700 ℃～800 ℃.
6. the production technique of superhigh carbon steel as claimed in claim 1 is characterized in that, earlier the reaction-injection moulding blank is put into the process furnace that reaches design temperature before the described hot rolling and is incubated, and soaking time is determined according to sotck thinkness, the corresponding 0.75mm of per minute.
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| CNB2004100255191A CN1325686C (en) | 2004-06-28 | 2004-06-28 | Process for producing super high carbon steel |
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Families Citing this family (5)
| Publication number | Priority date | Publication date | Assignee | Title |
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| CN103008659B (en) * | 2011-09-28 | 2015-04-01 | 宝山钢铁股份有限公司 | Manufacturing method of ultra-fine grain high-temperature alloy plate blanks |
| CN102836976B (en) * | 2012-09-19 | 2015-05-27 | 赵冰 | Preparation method for steel plate |
| CN104178693B (en) * | 2014-03-31 | 2017-04-05 | 浙江机电职业技术学院 | A kind of high-performance superhigh carbon steel and composite heat treating process |
| CN105018849A (en) * | 2015-08-13 | 2015-11-04 | 济宁市技师学院 | Aluminum-free ultra-high carbon steel and preparation method thereof |
| CN108866442B (en) * | 2018-07-19 | 2020-04-10 | 湖南长高新材料股份有限公司 | Heat treatment method for ultra-high carbon steel and product |
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US4448613A (en) * | 1982-05-24 | 1984-05-15 | Board Of Trustees, Leland Stanford, Jr. University | Divorced eutectoid transformation process and product of ultrahigh carbon steels |
| US4533390A (en) * | 1983-09-30 | 1985-08-06 | Board Of Trustees Of The Leland Stanford Junior University | Ultra high carbon steel alloy and processing thereof |
| US4769214A (en) * | 1985-09-19 | 1988-09-06 | Sptek | Ultrahigh carbon steels containing aluminum |
| US5445685A (en) * | 1993-05-17 | 1995-08-29 | The Regents Of The University Of California | Transformation process for production of ultrahigh carbon steels and new alloys |
| CN1367272A (en) * | 2001-09-30 | 2002-09-04 | 宝山钢铁股份有限公司 | Ultrahigh carbon steel base material with superplasticity, its production method and application |
| CN1417365A (en) * | 2002-11-29 | 2003-05-14 | 上海宝钢集团公司 | High-strength superhigh-carbon steel and its production process |
| CN1472358A (en) * | 2002-07-30 | 2004-02-04 | 宝山钢铁股份有限公司 | Non-tempered superhigh carbon steel and its production |
-
2004
- 2004-06-28 CN CNB2004100255191A patent/CN1325686C/en not_active Expired - Lifetime
Patent Citations (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US4448613A (en) * | 1982-05-24 | 1984-05-15 | Board Of Trustees, Leland Stanford, Jr. University | Divorced eutectoid transformation process and product of ultrahigh carbon steels |
| US4533390A (en) * | 1983-09-30 | 1985-08-06 | Board Of Trustees Of The Leland Stanford Junior University | Ultra high carbon steel alloy and processing thereof |
| US4769214A (en) * | 1985-09-19 | 1988-09-06 | Sptek | Ultrahigh carbon steels containing aluminum |
| US5445685A (en) * | 1993-05-17 | 1995-08-29 | The Regents Of The University Of California | Transformation process for production of ultrahigh carbon steels and new alloys |
| CN1367272A (en) * | 2001-09-30 | 2002-09-04 | 宝山钢铁股份有限公司 | Ultrahigh carbon steel base material with superplasticity, its production method and application |
| CN1472358A (en) * | 2002-07-30 | 2004-02-04 | 宝山钢铁股份有限公司 | Non-tempered superhigh carbon steel and its production |
| CN1417365A (en) * | 2002-11-29 | 2003-05-14 | 上海宝钢集团公司 | High-strength superhigh-carbon steel and its production process |
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Assignee: Jiangsu Baosteel Precision Steel Wire Co., Ltd. Assignor: Baoshan Iron & Steel Co., Ltd. Contract record no.: 2012320010047 Denomination of invention: Process for producing super high carbon steel Granted publication date: 20070711 License type: Exclusive License Open date: 20060104 Record date: 20120323 |