WO2017186113A1 - 一种复合防护用钢板及其制造方法 - Google Patents

一种复合防护用钢板及其制造方法 Download PDF

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WO2017186113A1
WO2017186113A1 PCT/CN2017/081953 CN2017081953W WO2017186113A1 WO 2017186113 A1 WO2017186113 A1 WO 2017186113A1 CN 2017081953 W CN2017081953 W CN 2017081953W WO 2017186113 A1 WO2017186113 A1 WO 2017186113A1
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steel
steel sheet
layer
composite
steel layer
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PCT/CN2017/081953
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English (en)
French (fr)
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宋凤明
温东辉
胡晓萍
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宝山钢铁股份有限公司
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Priority to DE112017002177.4T priority Critical patent/DE112017002177T5/de
Priority to US16/096,125 priority patent/US10882277B2/en
Priority to JP2019506774A priority patent/JP6743282B2/ja
Publication of WO2017186113A1 publication Critical patent/WO2017186113A1/zh

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    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B32—LAYERED PRODUCTS
    • B32B—LAYERED PRODUCTS, i.e. PRODUCTS BUILT-UP OF STRATA OF FLAT OR NON-FLAT, e.g. CELLULAR OR HONEYCOMB, FORM
    • B32B15/00—Layered products comprising a layer of metal
    • B32B15/01—Layered products comprising a layer of metal all layers being exclusively metallic
    • B32B15/011—Layered products comprising a layer of metal all layers being exclusively metallic all layers being formed of iron alloys or steels
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
    • B23P—METAL-WORKING NOT OTHERWISE PROVIDED FOR; COMBINED OPERATIONS; UNIVERSAL MACHINE TOOLS
    • B23P15/00—Making specific metal objects by operations not covered by a single other subclass or a group in this subclass
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B32—LAYERED PRODUCTS
    • B32B—LAYERED PRODUCTS, i.e. PRODUCTS BUILT-UP OF STRATA OF FLAT OR NON-FLAT, e.g. CELLULAR OR HONEYCOMB, FORM
    • B32B15/00—Layered products comprising a layer of metal
    • B32B15/01—Layered products comprising a layer of metal all layers being exclusively metallic
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B32—LAYERED PRODUCTS
    • B32B—LAYERED PRODUCTS, i.e. PRODUCTS BUILT-UP OF STRATA OF FLAT OR NON-FLAT, e.g. CELLULAR OR HONEYCOMB, FORM
    • B32B15/00—Layered products comprising a layer of metal
    • B32B15/04—Layered products comprising a layer of metal comprising metal as the main or only constituent of a layer, which is next to another layer of the same or of a different material
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B32—LAYERED PRODUCTS
    • B32B—LAYERED PRODUCTS, i.e. PRODUCTS BUILT-UP OF STRATA OF FLAT OR NON-FLAT, e.g. CELLULAR OR HONEYCOMB, FORM
    • B32B15/00—Layered products comprising a layer of metal
    • B32B15/18—Layered products comprising a layer of metal comprising iron or steel
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B32—LAYERED PRODUCTS
    • B32B—LAYERED PRODUCTS, i.e. PRODUCTS BUILT-UP OF STRATA OF FLAT OR NON-FLAT, e.g. CELLULAR OR HONEYCOMB, FORM
    • B32B37/00—Methods or apparatus for laminating, e.g. by curing or by ultrasonic bonding
    • B32B37/10—Methods or apparatus for laminating, e.g. by curing or by ultrasonic bonding characterised by the pressing technique, e.g. using action of vacuum or fluid pressure
    • 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
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/008—Heat treatment of ferrous alloys containing Si
    • C—CHEMISTRY; METALLURGY
    • 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
    • C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • 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
    • 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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • 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
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
    • 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
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • 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
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—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
    • 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
    • C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B32—LAYERED PRODUCTS
    • B32B—LAYERED PRODUCTS, i.e. PRODUCTS BUILT-UP OF STRATA OF FLAT OR NON-FLAT, e.g. CELLULAR OR HONEYCOMB, FORM
    • B32B2250/00—Layers arrangement
    • B32B2250/05—5 or more layers
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B32—LAYERED PRODUCTS
    • B32B—LAYERED PRODUCTS, i.e. PRODUCTS BUILT-UP OF STRATA OF FLAT OR NON-FLAT, e.g. CELLULAR OR HONEYCOMB, FORM
    • B32B2250/00—Layers arrangement
    • B32B2250/42—Alternating layers, e.g. ABAB(C), AABBAABB(C)
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B32—LAYERED PRODUCTS
    • B32B—LAYERED PRODUCTS, i.e. PRODUCTS BUILT-UP OF STRATA OF FLAT OR NON-FLAT, e.g. CELLULAR OR HONEYCOMB, FORM
    • B32B2311/00—Metals, their alloys or their compounds
    • B32B2311/30—Iron, e.g. steel
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B32—LAYERED PRODUCTS
    • B32B—LAYERED PRODUCTS, i.e. PRODUCTS BUILT-UP OF STRATA OF FLAT OR NON-FLAT, e.g. CELLULAR OR HONEYCOMB, FORM
    • B32B2571/00—Protective equipment
    • B32B2571/02—Protective equipment defensive, e.g. armour plates, anti-ballistic clothing
    • 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
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/008—Martensite

Definitions

  • the present invention relates to a steel sheet and a method of manufacturing the same, and more particularly to a composite steel sheet and a method of manufacturing the same.
  • Protective equipment or equipment such as cash transport vehicles have put forward protective requirements for key parts. It is required that the steel plate will not crack or penetrate when impacted by high-speed impact objects of impact materials within a certain distance.
  • Current protective materials include pure high-strength protective steel sheets, ceramic composite materials or high-molecular fiber materials.
  • the protective steel plate relies on high elastic deformation to absorb the impact energy of the impact material, and when the toughness is insufficient (especially the ultra high strength steel plate), it is easily broken and loses the protective function; the ceramic material has extremely high hardness, but the toughness is poor. When it is in contact with the impacting material, it is broken into smaller pieces to absorb the impact energy. It usually needs to be used together with the polymer fiber material. The latter has good toughness, and it is elastically deformed to absorb the impact load when impacting the impact. It is mostly used for protective vests. Production.
  • the publication number is CN1814845A, and the publication date is January 2, 2008.
  • the Chinese patent document entitled "A 1000MPa grade high-strength hot-rolled bulletproof steel plate and a manufacturing method thereof" discloses a 1000Mpa high-strength hot-rolled bulletproof steel plate.
  • the components are (% by weight): C 0.17 to 0.21%, Si 1.5 to 2.2%, Mn 1.5 to 2.0%, P ⁇ 0.035%, S ⁇ 0.010%, Al 0.015 to 0.060%, N ⁇ 0.0060%, Nb 0.010 ⁇ 0.050%, Ti 0.010-0.060%, Ca ⁇ 0.0050% can be added, and the rest are Fe and unavoidable impurities. It can be seen from the publication that the yield strength is only 1000 MPa, which is difficult to meet the protection requirements of the current market.
  • the publication number is CN102181795A, and the publication date is September 14, 2011.
  • the Chinese patent document entitled "An ultra-high-strength bullet-proof steel plate and its manufacturing process” discloses an ultra-high-strength bullet-proof steel plate and a manufacturing and forming process thereof.
  • the chemical composition is in terms of weight percent: C0.30 ⁇ 0.5, Si0.40 ⁇ 0.60, Mn 1.50 to 1.80, P ⁇ 0.025, S ⁇ 0.01, Cr + Ni + Mo ⁇ 2.5, Nb + V + Ti + B ⁇ 0.20, and the rest is Fe.
  • the bulletproof steel plate involved in this technical solution has a tensile strength of about 2000 MPa. Although it does not mention any toughness index, since the hardness value even exceeds 600HB, the excessive hardness makes the toughness of the steel plate lower, and the impact is withstood. It is extremely fragile when impacted.
  • One of the objects of the present invention is to provide a steel sheet for composite protection which has an excellent protective effect by a hard steel layer and a mild steel layer which are spaced apart from each other.
  • the present invention provides a composite protective steel sheet comprising: a hard steel layer and a soft steel layer which are spaced apart from each other, wherein the surface layer of the composite protective steel sheet is a hard steel layer, the hard steel layer and the soft layer
  • the atomic bonding is achieved by rolling composite between the steel layers; wherein the chemical element mass percentage of the soft steel layer is:
  • the unavoidable impurities are mainly P, S, and N elements, wherein P ⁇ 0.01%, S ⁇ 0.006%, and N ⁇ 0.005% can be controlled.
  • the composite protective steel plate according to the present invention is provided with a hard steel layer and a soft steel layer which are arranged at intervals, so that the hard steel layer is cracked into small pieces when subjected to impact by impact, and the impact work is consumed, and the soft steel layer changes the impact of the impact material.
  • the direction increases the resistance of the impacting material, thus achieving excellent protection.
  • the C content of the mild steel layer of the present invention is controlled to be between 0.001 and 0.01%.
  • the soft steel layer of the present invention has a Si content of not more than 0.005%.
  • Mn is also a common strengthening element in steel, and the yield strength is improved by solid solution strengthening to lower the elongation. Therefore, the Mn content of the mild steel layer of the present invention is controlled to be between 0.05 and 0.15%.
  • Al is an essential element for deoxidation, but it also increases the strength of the steel. Therefore, in the soft steel layer of the present invention
  • the Al content is controlled to be 0.005% or less.
  • Ti is used to immobilize C and N atoms to reduce their hindrance to dislocation motion.
  • Ti can form TiN ⁇ Ti4C2S2 ⁇ TiS and TiC in the steel in order to eliminate free C and N atoms in the steel, thereby reducing the yield strength.
  • the coarsening of TiC and TiN particles causes the grain boundary pinning effect to be lost, the grain size is increased, and the grain boundary strengthening effect is reduced.
  • more Ti will lower the elongation of the protective steel sheet. Therefore, the Ti content of the mild steel layer of the present invention is controlled to be 0.01 to 0.10%.
  • the matrix structure of the soft steel layer of the composite protective steel sheet is equiaxed ferrite.
  • the equiaxed ferrite of the composite protective steel sheet has a crystal grain size of 40 to 120 ⁇ m.
  • the soft steel layer has good plasticity.
  • the soft steel layer of the composite protective steel sheet has a yield strength of 80-180 MPa, a hardness of not more than 90 Hv, and an elongation of more than 40%.
  • the chemical element mass percentage of the hard steel layer is:
  • the unavoidable impurities are mainly P, S, and N elements, wherein P ⁇ 0.015%, S ⁇ 0.005%, and N ⁇ 0.005% can be controlled.
  • the C content of the hard steel layer of the present invention is limited to 0.40 to 0.50%.
  • the Si content is controlled at 0.1-0.3%.
  • Si has a high solid solubility in steel, which can increase the volume fraction of ferrite in the steel and refine the grains, which is beneficial to improve the toughness. However, if the content is too high, the weldability will decrease. .
  • Mn has a strong solid solution strengthening effect, while significantly reducing the phase transition temperature of steel, refining the microstructure of steel, is an important strengthening and toughening element, but excessive Mn content increases the hardenability, resulting in The toughness of the weldability and weld heat affected zone deteriorates, so the content is controlled to be 1.0-1.5%.
  • Al is added as a deoxidizer during the steel making process, and a small amount of Al is also beneficial for refining the grains and improving the toughness of the steel.
  • too high Al will increase the brittleness of the ferrite in the steel and lead to a decrease in the toughness of the steel, so the content is controlled to be 0.01-0.05%.
  • Cr has a solid solution strengthening effect, but Cr is a precious alloying element. Therefore, the Cr content of the hard steel layer of the present invention is limited to 0.1 to 0.3%.
  • Ni can not only improve the strength of the steel sheet but also improve the toughness of the steel sheet, but Ni is a precious alloying element. Therefore, the hard steel layer of the present invention has a Ni-defined content of 0.1 to 0.3%.
  • Ti mainly inhibits the austenite grain growth during the reheating of the slab, and inhibits the growth of ferrite grains during recrystallization and rolling, and improves the toughness of the steel.
  • the B content of the hard steel layer of the present invention is limited to 0.001 to 0.003%.
  • the hard steel layer of the present invention has a Mo content of 0.05 to 0.5%.
  • the base structure of the hard steel layer of the composite protective steel sheet is martensite.
  • the hard steel layer of the composite protective steel sheet has a yield strength greater than 2000 MPa and a hardness greater than 600 HBW.
  • the hard steel layer of the composite protective steel plate adopts a high C content and adds Mo and B elements for improving hardenability, and the heat resistance can make the matrix structure high strength Markov.
  • Body yield strength greater than 2000MPa, hardness greater than 600HBW.
  • the composite protective steel sheet has two layers of hard steel layer with the facing layer and a layer of mild steel layer disposed between the two layers of hard steel layers. That is, in this embodiment, the steel sheet for composite protection has three layers.
  • the soft steel layer of the composite protective steel sheet has at least two layers. That is, in this embodiment, the steel sheet for composite protection has five layers.
  • the composite sandwich panel design of the composite protective steel plate can determine the specific number of layers according to different protection requirements.
  • the composite protective steel sheet according to the present invention has a thickness of 2-20 mm, and the composite protective steel sheet according to the present invention has better protection performance under the same specifications as compared with the conventional protective steel sheet.
  • Another object of the present invention is to provide a method for producing the above-mentioned composite protective steel sheet, by which a composite protective steel sheet excellent in performance can be produced.
  • the present invention also provides a method for manufacturing a composite protective steel sheet, comprising the steps of:
  • the hard steel layer blank and the mild steel layer blank are preferably subjected to surface cleaning work before the assembly.
  • the surface cleaning method may be carried out using a wire brush or a sanding belt, a direct pickling method, or a surface cleaning method in a manner conceivable by those skilled in the art.
  • the number of layers of the hard steel layer blank and the soft steel layer blank can be determined according to specific needs.
  • the composite protective steel sheet is oxidized during the heating process, in the technical solution, when the hard steel layer blank and the soft steel layer blank are subjected to interlayer welding, the welding is performed directly under vacuum in the vacuum chamber instead of Vacuum welding, which is often used in the prior art, reduces the difficulty of production and effectively prevents oxidation.
  • the ratio of the thickness of the single layer of the mild steel layer blank to the hard steel layer blank is 0.5-0.8, and the ratio of the total thickness of the soft steel layer blank to the total thickness of the hard steel layer blank is 0.15-0.40. .
  • the thickness ratio between the mild steel layer blank and the hard steel layer blank is designed such that the composite steel sheet has sufficient energy dissipation effect and the invading impact material changes direction of advancement, thereby improving the protective effect.
  • step (3) of the method for producing a composite protective steel sheet it is heated in the range of 1100 to 1200 ° C, held for 2-3 hours, and then subjected to composite rolling to control the finish rolling temperature to be 850 to 900 ° C.
  • the method for producing a composite protective steel sheet is air-cooled or water-cooled to 650-750 ° C after rolling.
  • the quenching temperature is at least 50 ° C above the Ac3 temperature of the hard steel layer, and the holding time is at least 3 mm/min ⁇ composite steel sheet
  • the thickness, thickness in mm is then cooled to room temperature at a rate of ⁇ 50 ° C / s.
  • the quenching temperature is controlled to be at least 50 ° C above the Ac3 temperature of the hard steel layer, the holding time is at least 3 mm / min ⁇ the thickness of the composite steel plate, the thickness is in mm, and then cooled to room temperature at a rate of ⁇ 50 ° C / s because:
  • the temperature is above Ac3, the microstructure of the steel matrix begins to austenitize.
  • the method for producing a composite protective steel sheet has a tempering temperature of 150 to 230 ° C and a holding time of 15 to 60 minutes.
  • the composite protective steel sheet according to the present invention is tempered in the interval of 150-230 ° C for the purpose of slowing down and eliminating the quenching stress and improving the toughness of the composite protective steel sheet.
  • the composite protective steel plate according to the present invention adopts a cross design of soft and hard steel layers, and has a multi-layer structure, wherein the hard steel layer of the outer layer is subjected to impact deformation, cracking or even detachment of the impact object, and the deformation work,
  • the crack formation and expansion work, the interlayer bonding energy and the detachment kinetic energy of the inner layer of the soft steel layer fully absorb and consume part of the kinetic energy of the impact material, so that the impact material loses the forward ability; and the inner soft steel layer has good plasticity, Excellent deformation ability, so that the impact material changes the direction of advancement, increasing the penetration thickness of the impact object, and further reducing the damage of the impact object.
  • the composite steel sheet according to the present invention is a rolled composite steel sheet, the interlayer metal realizes atomic bonding at a high temperature, and the interlayer bonding strength is high and it is difficult to delaminate.
  • a single layer of soft steel layer blank and a single layer of hard steel layer blank are required
  • the thickness ratio of the single layer is 0.5-0.8, and the total thickness ratio of the soft and hard steel is 0.15-0.40, so that the soft steel layer has a certain thickness to ensure that the impact material changes direction when the impact material invades, and the damage ability and danger degree of the impact object are reduced.
  • the thickness of the outer hard steel layer can be symmetrically designed to keep the thickness of the upper and lower hard steel layers uniform, or an asymmetric design, that is, the thickness of the upper and lower hard steel layers can be different to further improve the protection effect.
  • the intermediate layer of mild steel according to the present invention is designed with a very low C-Si-Mn composition, while controlling the Al content at a lower level, and supplemented with an appropriate Ti element, so that the intermediate soft layer steel plate is even in quenching conditions.
  • the lower hardness value does not exceed 90 Hv.
  • the number of layers of the soft and hard steel plate of the composite protective steel plate according to the present invention is flexible and adjustable, and the specific number of layers can be determined according to different protection requirements, and may be 3 layers or 5 layers or more, and the overall thickness can be Adjust to meet the protection needs under different conditions.
  • the composite protective steel sheet according to the present invention adopts a soft and hard layer cross design, thereby improving the plasticity of the protective steel sheet, having better cold bending processing performance, and increasing the application range of the protective steel sheet.
  • the manufacturing method of the present invention employs a vacuum welding edge-sealing technique in the assembly step of the composite steel sheet, thereby avoiding the vacuuming process after the conventional welding and having a better sealing effect.
  • the manufacturing method of the present invention adopts a conventional hot rolling process like the ordinary steel slab after the step of the slab, thereby improving the applicability, reducing the production difficulty and the production cost.
  • the impact agents described herein are bullets or pellets.
  • the protective or protective capabilities described herein are bulletproof or ballistic resistant.
  • the protective steel sheet of the present invention is a bulletproof steel sheet.
  • Fig. 1 is a schematic view showing the structure of a steel sheet for composite protection of Example A2.
  • Figure 3 is a photograph of the metallographic structure of the mild steel layer of Example A1.
  • Example 4 is a photograph of the metallographic structure of the hard steel layer of Example A1.
  • Figure 5 is a photograph of the metallographic structure of the mild steel layer of Example A2.
  • Figure 6 is a photograph of the metallographic structure of the hard steel layer of Example A2.
  • Table 1 lists the mass percentages of the chemical elements in the composite protective steel sheets Examples A1-A6.
  • Fig. 1 is a view schematically showing the structure of an embodiment A2 of the present invention.
  • the steel sheet for composite protection has a five-layer structure, wherein two layers and two layers are soft steel layers, 3, 5 and 3 layers are hard steel layers, and the hard steel layer and the soft steel layer are spaced apart from each other.
  • Hard steel layer blanks and mild steel layer blanks are prepared according to the ingredients listed in Table 1.
  • coiling temperature is 650-750 ° C
  • the quenching temperature is at least 50 ° C above the Ac3 temperature of the hard steel layer
  • the holding time is at least 3 mm / min ⁇ the thickness of the composite steel plate, the thickness unit is mm, and then ⁇ 50 ° C / s
  • the temperature is cooled to room temperature
  • the tempering temperature is 150-230 ° C
  • the holding time is 15-60 min.
  • Table 2 lists the thickness and interlayer design of the hard steel layer blank and the mild steel layer blank of the composite in the composite protective steel sheets Examples A1-A6.
  • the single layer thickness ratio of the mild steel layer blank and the hard steel layer blank of Examples A1 to A6 is controlled to be 0.5-0.8, and the total thickness ratio of the mild steel layer blank to the hard steel layer blank is 0.15. -0.40.
  • the composite sandwich panel has flexible design and can be determined according to different protection requirements, and can be 3 layers or more layers.
  • the steel plate has sufficient energy dissipation and changes the intrusive impact material to the forward direction, thereby improving the protective effect.
  • Table 3 lists the process parameters of the manufacturing methods of Examples A1-A6.
  • the yield strength of the hard steel layers of Examples A1 - A6 was ⁇ 2000 MPa, the hardness of the hard steel layer exceeded 600 HBW, and the yield of the mild steel layer of Examples A1 - A6
  • the strength is not more than 180MPa, the elongation is above 40%, and the hardness values are not more than 90Hv, so it has good plasticity.
  • FIG. 2 is a CCT curve of the soft steel layer of the steel sheet for composite protection according to the present invention, and it can be seen from the curve that the soft steel layer can obtain equiaxed ferrite in a quenched state.
  • Fig. 3 shows the matrix structure of the mild steel layer of Example A1. It can be seen from Fig. 3 that the matrix structure of the mild steel layer is equiaxed ferrite.
  • Figure 4 shows the matrix structure of the hard steel layer of Example A1. It can be seen from Figure 4 that the hard steel layer matrix structure is mainly martensite.
  • Figure 5 shows the matrix structure of the mild steel layer of Example A2. It can be seen from Figure 5 that the soft steel layer matrix structure is equiaxed ferrite.
  • Figure 6 shows the matrix structure of the hard steel layer of Example A2. It can be seen from Figure 6 that the matrix structure of the hard steel layer is mainly martensite.

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Abstract

一种复合防护用钢板，包括：相互间隔设置的硬钢层（1、3、5）和软钢层（2、4），其中复合防护用钢板的面层为硬钢层（1、3、5），硬钢层（1、3、5）与软钢层（2、4）之间通过轧制复合实现原子结合；其中，软钢层（2、4）的化学元素质量百分比为：C：0.001-0.01％，0＜Si≤0.005％，Mn：0.05-0.15％，0＜Al≤0.005％，Ti：0.01-0.10％，余量为Fe和其他不可避免的杂质。

Description

一种复合防护用钢板及其制造方法 技术领域
本发明涉及一种钢板及其制造方法，尤其涉及一种复合钢板及其制造方法。
背景技术
运钞车等防护器具或设备对关键部位均提出了防护要求，要求在一定距离内钢板承受冲击物高速冲击物冲击时不开裂或不贯穿。目前的防护材料包括单纯的高强度防护用钢板、陶瓷复合材料或高分子纤维材料。其中防护用钢板依靠高的弹性变形吸收冲击物的冲击功，在韧性不足时(特别是超高强度钢板)极易碎裂而失去防护功能；陶瓷材料具有极高的硬度，但韧性很差，在与冲击物接触时碎裂为更小的碎片从而吸收冲击能，通常需要与高分子纤维材料一起使用，后者韧性好，承受冲击物冲击时发生弹性变形而吸收冲击载荷，多用于防护背心的制作。
理论上，单纯使用足够厚的钢板能够满足不同条件下的防护要求，但过厚的钢板增加了重量，牺牲了机动性，同时增加能耗。目前，防护用钢板朝着更高强度、更薄厚度方向发展。
公开号为CN1814845A，公开日为2008年1月2日，名称为“一种1000MPa级高强度热轧防弹钢板及其制造方法”的中国专利文献公开了一种1000Mpa级高强度热轧防弹钢板，其成分是(重量百分比)：C 0.17～0.21％、Si 1.5～2.2％、Mn 1.5～2.0％、P≤0.035％、S≤0.010％、Al 0.015～0.060％、N≤0.0060％、Nb 0.010～0.050％、可加入Ti 0.010～0.060％、Ca≤0.0050％，其余是Fe和不可避免的杂质。从该公开文献可以看出，其屈服强度仅为1000MPa，难以满足当前市场的防护要求。
公开号为CN102181795A，公开日为2011年9月14日，名称为“一种超高强度防弹钢板及其制造工艺”的中国专利文献公开了一种超高强度防弹钢板及其制造成形工艺,其化学成分按重量百分比计为：C0.30～0.5、Si0.40～0.60、 Mn1.50～1.80、P≤0.025、S≤0.01、Cr+Ni+Mo≤2.5、Nb+V+Ti+B≤0.20,其余是Fe。这个技术方案所涉及的防弹钢板具有约2000MPa的抗拉强度，虽然其并没有提及任何韧性指标，但是由于其硬度值甚至超过了600HB，因此过高的硬度使得钢板的韧性降低，在承受冲击物冲击时极易碎裂。
因此，需要提供一种在确保防护用钢板的强度的前提下，降低钢板的厚度，并改善钢板的韧性的防护用钢板产品。
发明内容
本发明的目的之一在于提供一种复合防护用钢板，其通过相互间隔设置的硬钢层和软钢层，使得其具有优秀的防护效果。
为了实现上述目的，本发明提出了一种复合防护用钢板，包括：相互间隔设置的硬钢层和软钢层，其中复合防护用钢板的面层为硬钢层，所述硬钢层与软钢层之间通过轧制复合实现原子结合；其中，所述软钢层的化学元素质量百分比为：
C：0.001-0.01％,0＜Si≤0.005％,Mn：0.05-0.15％,0＜Al≤0.005％,Ti：0.01-0.10％，余量为Fe和其他不可避免的杂质。
在本发明所述的复合防护用钢板的所述软钢层中，不可避免的杂质主要是P、S、N元素，其中可以控制P≤0.01％，S≤0.006％，N≤0.005％。
本发明所述的复合防护用钢板通过设置间隔设置的硬钢层和软钢层，使得硬钢层在承受冲击物冲击时开裂为小的碎片，消耗冲击功，同时软钢层改变冲击物行进方向，增加冲击物前进阻力，从而实现了优秀的防护效果。
本发明所述的软钢层中的各化学元素的设计原理为：
C通过固溶强化会使屈服强度升高，延伸率降低。根据实际的炼钢工艺，应尽可能降低其含量，因此，本发明所述软钢层的C含量控制在0.001-0.01％之间。
Si为脱氧元素，也是固溶强化元素，使屈服强度升高，延伸率降低，所以要尽量降低Si的添加量。因此，本发明所述软钢层的Si含量不超过0.005％。
Mn也是钢中常见的强化元素，通过固溶强化提高屈服强度，使延伸率降低。因此，本发明所述软钢层的Mn含量控制在0.05-0.15％之间。
Al是脱氧必需的元素，但也会提高钢的强度。因此，本发明所述软钢层中 Al含量控制在0.005％以下。
Ti用来固定C、N原子以降低其对位错运动的阻碍作用。Ti在钢中可依次形成TiN→Ti4C2S2→TiS和TiC，消除钢中自由的C、N原子，从而降低屈服强度。同时TiC、TiN等颗粒的粗化使其失去了晶界钉扎效应，增大了晶粒尺寸，降低了晶界强化效果。但较多的Ti会降低防护用钢板的延伸率。因此，本发明所述软钢层Ti含量控制在:0.01-0.10％。
进一步地，所述的复合防护用钢板的所述软钢层的基体组织为等轴状铁素体。
更进一步地，所述的复合防护用钢板的所述等轴状铁素体的晶粒尺寸为40-120μm。
在本技术方案中，由于采用极低的C-Si-Mn成分设计并通过Ti固定C、N间隙原子，消除了C、N原子的固溶强化作用，并利用粗化的TiN、TiC颗粒获得较大的晶粒尺寸，从而使得所述的复合防护用钢板的所述软钢层的基体组织即使在淬火状态下仍为等轴状铁素体，所述等轴状铁素体的晶体尺寸40-120μm，即使在淬火条件下所述软钢层的硬度值不超过90Hv。从而使得软钢层具有良好的塑性。
在本技术方案中，所述的复合防护用钢板的所述软钢层的屈服强度为80-180MPa，硬度不超过90Hv，延伸率大于40％。
进一步地，在本发明所述的复合防护用钢板中，所述硬钢层的化学元素质量百分比为：
C：0.40-0.50％,Si：0.1-0.3％，Mn：1.0-1.5％,Al：0.01-0.05％,Cr：0.1-0.3％，Ni：0.1-0.3％，Ti：0.01-0.03％，B：0.001-0.003％，Mo：0.05-0.5％，余量为Fe和其他不可避免的杂质。
在本发明所述的复合防护用钢板的所述硬钢层中，不可避免的杂质主要是P、S、N元素，其中可以控制P≤0.015％，S≤0.005％，N≤0.005％。
上述方案中，所述的复合防护用钢板的所述硬钢层中的各化学元素的设计原理为：
C是钢中最廉价的强化元素，但过高的C使得高温的防护用钢板的钢坯易在冷却过程中开裂，不利于防护用钢板的钢坯的保存，增加了生产难度。因此，本发明所述硬钢层的C含量限定为0.40-0.50％。
Si含量控制在0.1-0.3％，Si在钢中具有较高的固溶度，能够增加钢中铁素体体积分数，细化晶粒，因而有利于提高韧性，但含量过高将导致焊接性能下降.
Mn具有较强的固溶强化作用，同时显著降低钢的相变温度，细化钢的显微组织，是重要的强韧化元素，但是Mn含量过多使淬透性增大，从而导致可焊性和焊接热影响区韧性恶化，所以将其含量控制在1.0-1.5％。
Al在炼钢过程中作为脱氧剂添加，同时微量的Al同时有利于细化晶粒，改善钢材的强韧性能。但过高的Al将使钢中铁素体脆性增加而导致钢韧性的降低，所以控制其含量0.01-0.05％。
Cr具有固溶强化效果，但是Cr是贵重合金元素。因此，本发明所述硬钢层的Cr含量限定为0.1-0.3％。
Ni不仅可以提高钢板强度还可以改善钢板韧性，但是Ni是贵重合金元素。因此，本发明所述硬钢层的Ni限定含量为0.1-0.3％。
添加0.01-0.03％Ti主要是抑制板坯再热过程中的奥氏体晶粒长大，同时在再结晶控轧过程中抑制铁素体晶粒长大，提高钢的韧性。
B具有良好的淬透性，从而提高钢板硬度，然而B含量过高对焊接不利。因此，本发明所述硬钢层的B含量限定为0.001-0.003％
Mo具有良好的淬透性，可以提高钢板硬度，但Mo为贵重合金元素。因此，本发明所述硬钢层的Mo限定含量为0.05-0.5％。
进一步地，所述的复合防护用钢板的所述硬钢层的基体组织为马氏体。
进一步地，所述的复合防护用钢板的所述硬钢层的屈服强度大于2000MPa，硬度大于600HBW。
在本技术方案中，所述复合防护用钢板的所述硬钢层采用较高的C含量并添加了提高淬透性的Mo、B元素，在热处理后可以使得基体组织为高强度的马氏体，屈服强度大于2000MPa，硬度大于600HBW。
在一种实施方式下，所述复合防护用钢板具有这与面层的两层硬钢层以及设置于两层硬钢层之间的一层软钢层。也就是说，在该实施方式中，复合防护用钢板具有三层。
进一步地，所述的复合防护用钢板的所述软钢层至少有两层。也就是说，在该实施方式中，复合防护用钢板具有五层。
在本技术方案中，所述的复合防护用钢板的组坯夹层设计，可以根据不同的防护要求确定具体的层数。
进一步地，本发明所述的复合防护用钢板的厚度为2-20mm，较之于现有的防护用钢板，同样规格条件下本发明所述的复合防护用钢板具有更好的防护性能。
本发明的另一目的还在于提供一种可以制造上述复合防护用钢板的制造方法，采用该方法可以生产出性能优良的复合防护用钢板。
为了达到上述发明目的，本发明还提出了一种复合防护用钢板的制造方法，其包括步骤：
(1)将硬钢层坯料和软钢层坯料组坯；
(2)真空焊接；
(3)复合轧制；
(4)轧后空冷或水冷；
(5)卷取；
(6)开卷、矫直和切板；
(7)进行淬火和回火热处理。
本技术方案中，由于硬钢层坯料和软钢层坯料的结合面上的氧化层与油污，因此硬钢层坯料和软钢层坯料在组坯前最好进行表面清理工作。表面清理方法可以采用钢丝刷或砂带进行，也可以采用直接酸洗的方法，也可以是本领域内技术人员能够想到的方式进行表面清理的。
本技术方案中硬钢层坯料和软钢层坯料组坯层数可以根据具体需要确定。
由于复合防护用钢板在加热过程中会产生氧化，因此，在本技术方案中，硬钢层坯料和软钢层坯料周边进行层间焊接时，直接在真空室的真空状态下进行焊接，而不是现有技术中经常采用的抽真空焊接，这种方式降低了生产难度，有效防止了氧化。
进一步地，在所述步骤(1)中，软钢层坯料与硬钢层坯料的单层厚度比为0.5-0.8，软钢层坯料总厚度与硬钢层坯料总厚度的比为0.15-0.40。
在本技术方案中，软钢层坯料与硬钢层坯料之间的厚度比的设计使得所述复合钢板具有充分的消能作用并使侵入的冲击物改变前进方向，从而提高防护效果。
进一步地，在所述复合防护用钢板的制造方法的步骤(3)中，在1100～1200℃范围内加热，保温2-3h，然后复合轧制，控制终轧温度为850～900℃。
更进一步地，所述的复合防护用钢板的制造方法在所述步骤(4)中，轧后空冷或水冷至650-750℃。
在本技术方案中，轧后根据成品厚度采取水冷或是空冷，一般较薄的钢板可以采取空冷。
进一步地，所述的复合防护用钢板的制造方法在所述步骤(7)中的淬火步骤中，淬火温度为硬钢层的Ac3温度以上至少50℃，保温时间至少为3mm/min×复合钢板的厚度，厚度单位为mm，然后以≥50℃/s的速度冷却至室温。
将淬火温度温度控制为硬钢层的Ac3温度以上至少50℃，保温时间至少为3mm/min×复合钢板的厚度，厚度单位为mm，然后以≥50℃/s的速度冷却至室温是因为：温度在Ac3以上时，钢基体中组织开始奥氏体化，超过Ac3的温度越高，奥氏体化的驱动力越高，则奥氏体化的速度越快，保温时间越短，但淬火加热温度过高增加能耗，提高生产成本。所以限定淬火温度在Ac3温度以上50℃，保温时间为钢板厚度的3倍。
更进一步地，所述的复合防护用钢板的制造方法在所述步骤(7)中的回火步骤中，回火温度为150-230℃，保温时间15-60min。
本发明所述的复合防护用钢板在150-230℃区间进行回火处理，目的在于减缓、消除淬火应力，改善所述复合防护用钢板的韧性。
本发明所述的复合防护用钢板具有如下有益效果：
(1)本发明所述的复合型防护用钢板采用软、硬钢层交叉设计，具有多层结构，其中外层的硬钢层在承受冲击物冲击性变形、开裂甚至脱离，其变形功、裂纹形成及扩展功、与内层软钢层脱离的层间结合能及碎片脱离动能等充分吸收、消耗了冲击物部分动能，使冲击物失去前进能力；而内侧的软钢层塑性好，具有优良的变形能力，从而使得冲击物改变前进方向，增加冲击物的穿透厚度，进一步减轻冲击物的破坏。
(2)本发明所述的复合钢板由于是轧制复合钢板，因此层间金属在高温下实现了原子结合，其层间结合强度高，不易分层。
(3)在本发明的优选方案中，要求单层软钢层坯料与单层硬钢层坯料的 单层厚度比0.5-0.8，软硬钢的总厚度比在0.15-0.40，从而使得软钢层具有一定的厚度以保证冲击物侵入时使冲击物改变方向，降低冲击物的破坏能力和危险程度，提高了复合钢板的防护能力。其中外层硬钢层的厚度既可对称设计，保持上下层硬钢层厚度一致，也可以采用非对称设计，即上下层硬钢层厚度不等，以进一步提高防护效果。
(4)本发明涉及的中间层软钢采用极低的C-Si-Mn成分设计，同时控制Al含量在较低的水平，并辅以适当的Ti元素，使得中间软层钢板即使在淬火条件下硬度值也不超过90Hv。
(5)本发明所述的复合型防护用钢板的软硬钢板层数灵活可调，可以根据不同的防护要求确定具体的层数，可以为3层或5层甚至更多，同时总体厚度可调，从而满足不同条件下的防护需求。
(6)本发明涉及的复合型防护用钢板采用软硬层交叉设计，从而使得防护用钢板的塑性得以改善，具有更好的冷弯加工性能，增加了防护用钢板的应用范围。
本发明所述的复合防护用钢板的制造方法具有如下有益效果：
(1)本发明所述的制造方法在复合钢板的组坯步骤采用了真空焊接封边技术，避免了常规焊接后的抽真空过程，具有更好的密封效果。
(2)本发明所述的制造方法在组坯步骤后，与普通钢坯一样采用了常规的热轧工艺，从而提高了其适用性，降低了生产难度及生产成本。
应理解，在某些优选的实施方案中，本文所述的冲击物是子弹或弹丸。在某些实施方案中，本文所述的防护效果或防护能力为防弹效果或防弹能力。在某些优选的实施方案中，本发明的防护用钢板是防弹钢板。
附图说明
图1为实施例A2的复合防护用钢板的结构示意图。
图2为本发明所述的复合防护用钢板的所述软钢层的CCT曲线(连续冷却转变曲线)。
图3为实施例A1的软钢层的金相组织照片。
图4为实施例A1的硬钢层的金相组织照片。
图5为实施例A2的软钢层的金相组织照片。
图6为实施例A2的硬钢层的金相组织照片。
具体实施方式
下面将结合附图说明和具体的实施例对本发明所述的复合防护用钢板及其制造方法做进一步的解释和说明，然而该解释和说明并不对本发明的技术方案构成不当限定。
实施例A1-A6
表1列出了复合防护用钢板实施例A1-A6中的化学元素的质量百分比。
表1.(wt％，余量为Fe和除了P、S、N以外的其他杂质)
Figure PCTCN2017081953-appb-000001
图1示意性地显示了本发明实施例A2的结构，从图中可以看出，在该实施例中，复合防护用钢板具有五层结构，其中2、4两层为软钢层，1、3、5三层为硬钢层，且硬钢层与软钢层相互间隔设置。
上述实施例中的复合防护用钢板采用以下步骤制得：
(1)按表1所列的成分制得硬钢层坯料和软钢层坯料
(2)将硬钢层坯料和软钢层坯料组坯；
(3)在真空室内真空焊接；
(4)复合轧制：在1100～1200℃范围内加热，保温2-3h，然后复合轧制，控制终轧温度为850～900℃；
(5)轧后空冷或水冷至650-750℃；
(6)卷取，卷取温度为650-750℃；
(7)开卷、矫直和切板；
(8)进行淬火和回火热处理；淬火温度为硬钢层的Ac3温度以上至少50℃，保温时间至少为3mm/min×复合钢板的厚度，厚度单位为mm，然后以≥50℃/s的速度冷却至室温，回火温度为150-230℃，保温时间15-60min。
表2列出了复合防护用钢板实施例A1-A6中组坯的硬钢层坯料和软钢层坯料的厚度和夹层设计。
表2
Figure PCTCN2017081953-appb-000002
Figure PCTCN2017081953-appb-000003
从表2中可以看出，实施例A1-A6的软钢层坯料与硬钢层坯料的单层厚度比控制在了0.5-0.8，软钢层坯料与硬钢层坯料的总厚度比为0.15-0.40。所述的复合防护用钢板的组坯夹层设计灵活可调，可以根据不同的防护要求确定具体的层数，可以为3层或是3层以上的更多层数，这样的设计使得所述复合钢板具有充分的消能作用并使侵入的冲击物改变前进方向，从而提高防护效果。
表3列出了实施例A1-A6制造方法的工艺参数。
表3
Figure PCTCN2017081953-appb-000004
对复合防护用钢板实施例A1-A6的硬钢层和软钢层进行了力学性能测定，并将其结果列于表4。
表4
Figure PCTCN2017081953-appb-000005
从表4中可以看出，实施例A1-A6的所述硬钢层的屈服强度均≥2000MPa，硬钢层的硬度都超过了600HBW，而实施例A1-A6的所述软钢层的屈服强度均不超过180MPa，延伸率均在40％以上，硬度值均不超过90Hv，因此具有良好的塑性。
图2为本发明所述的复合防护用钢板的所述软钢层的CCT曲线，通过该曲线可以得知软钢层在淬火状态下可获得等轴状铁素体。
图3显示了实施例A1的软钢层的基体组织，由图3可看出软钢层的基体组织为等轴状铁素体。
图4显示了实施例A1的硬钢层的基体组织，由图4可看出硬钢层基体组织主要为马氏体。
图5显示了实施例A2的软钢层的基体组织，由图5可看出软钢层基体组织为等轴状铁素体。
图6显示了实施例A2的硬钢层的基体组织，由图6可看出硬钢层的基体组织主要为马氏体。
需要注意的是，以上列举的仅为本发明的具体实施例，显然本发明不限于以上实施例，随之有着许多的类似变化。本领域的技术人员如果从本发明公开的内容直接导出或联想到的所有变形，均应属于本发明的保护范围。

Claims (16)

  1. 一种复合防护用钢板，其特征在于，包括：相互间隔设置的硬钢层和软钢层，其中复合防护用钢板的面层为硬钢层，所述硬钢层与软钢层之间通过轧制复合实现原子结合；其中，所述软钢层的化学元素质量百分比为：
    C：0.001-0.01％,0＜Si≤0.005％,Mn：0.05-0.15％,0＜Al≤0.005％,Ti：0.01-0.10％，余量为Fe和其他不可避免的杂质。
  2. 如权利要求1所述的复合防护用钢板，其特征在于，所述软钢层的基体组织为等轴状铁素体。
  3. 如权利要求2所述的复合防护用钢板，其特征在于，所述等轴状铁素体的晶粒尺寸为40-120μm。
  4. 如权利要求3所述的复合防护用钢板，其特征在于，所述软钢层的屈服强度为80-180MPa，硬度不超过90Hv，延伸率大于40％。
  5. 如权利要求1-4中任意一项所述的复合防护用钢板，其特征在于，所述硬钢层的化学元素质量百分比为：
    C：0.40-0.50％,Si：0.1-0.3％，Mn：1.0-1.5％,Al：0.01-0.05％,Cr：0.1-0.3％，Ni：0.1-0.3％，Ti：0.01-0.03％，B：0.001-0.003％，Mo：0.05-0.5％，余量为Fe和其他不可避免的杂质。
  6. 如权利要求5所述的复合防护用钢板，其特征在于，所述硬钢层的基体组织为马氏体。
  7. 如权利要求6所述的复合防护用钢板，其特征在于，所述硬钢层的屈服强度大于2000MPa，硬度大于600HBW。
  8. 如权利要求1所述的复合防护用钢板，其特征在于，所述复合防护用钢板具有这与面层的两层硬钢层以及设置于两层硬钢层之间的一层软钢层。
  9. 如权利要求1所述的复合防护用钢板，其特征在于，所述软钢层至少有两层。
  10. 如权利要求1所述的复合防护用钢板，其特征在于，其厚度为2-20mm。
  11. 如权利要求1-10中任意一项所述的复合防护用钢板的制造方法，其特征在于，包括步骤：
    (1)将硬钢层坯料和软钢层坯料组坯；
    (2)真空焊接；
    (3)复合轧制；
    (4)轧后空冷或水冷；
    (5)卷取；
    (6)开卷、矫直和切板；
    (7)进行淬火和回火热处理。
  12. 如权利要求11所述的复合防护用钢板的制造方法，其特征在于，在所述步骤(1)中，软钢层坯料与硬钢层坯料的单层厚度比为0.5-0.8，软钢层坯料总厚度与硬钢层坯料总厚度的比为0.15-0.40。
  13. 如权利要求11所述的复合防护用钢板的制造方法，其特征在于，在所述步骤(3)中，在1100～1200℃范围内加热，保温2-3h，然后复合轧制，控制终轧温度为850～900℃。
  14. 如权利要求11所述的复合防护用钢板的制造方法，其特征在于，在所述步骤(4)中，轧后空冷或水冷至650-750℃。
  15. 如权利要求11所述的复合防护用钢板的制造方法，其特征在于，在所述步骤(7)中的淬火步骤中，淬火温度为硬钢层的Ac3温度以上至少50℃，保温时间至少为3mm/min×复合钢板的厚度，厚度单位为mm，然后以≥50℃/s的速度冷却至室温。
  16. 如权利要求11或15所述的复合防护用钢板的制造方法，其特征在于，在所述步骤(7)中的回火步骤中，回火温度为150-230℃，保温15-60min。
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WO2018210574A1 (de) * 2017-05-16 2018-11-22 Thyssenkrupp Steel Europe Ag DREILAGIGER VERSCHLEIßSTAHL ODER SICHERHEITSSTAHL, VERFAHREN ZUR HERSTELLUNG EINER KOMPONENTE UND VERWENDUNG
CN109158839A (zh) * 2018-09-29 2019-01-08 安徽新芜精密装备制造产业技术研究院有限公司 一种电真空用ZGMn13的车削加工工艺
EP3754290B1 (de) 2019-06-17 2022-05-11 Benteler Automobiltechnik GmbH Verfahren zur herstellung eines panzerungsbauteils für kraftfahrzeuge
CN111331963A (zh) * 2020-03-27 2020-06-26 嘉兴吉森科技有限公司 一种多层复合钢及多层复合钢刀具的制作方法
CN111331963B (zh) * 2020-03-27 2024-01-05 嘉兴吉森科技有限公司 一种多层复合钢及多层复合钢刀具的制作方法

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US10882277B2 (en) 2021-01-05

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