High thermal diffusivity, high toughness and low crack risk during heat treatment tool steel

The present invention relates to a tool steel as described in WO2012095532A1 or WO2010112319A1 and its heat treatment where high levels of thermal diffusivity, mechanical resistance, wear resistance and/or toughness are attained while having a low cracking risk during the heat treatment. It is achieved by austenitizing at a temperature, normally above AC 3 , cooling to an intermediate temperature below AC 1 and above the temperature where bainitic (and alike) transformation occurs and finally quenching with a severe cooling media to a temperature below the bainitic transformation nose. Final microstructure is mainly composed of martensite and/or lower bainite, which will generally be afterwards tempered.

HOT-BAND ANNEALING EQUIPMENT, HOT-BAND ANNEALING METHOD AND DESCALING METHOD FOR SI-CONTAINING HOT ROLLED STEEL SHEET

Provided is a hot-band annealing method comprising subjecting a Si-containing hot rolled steel sheet, having an oxidized scale formed on a surface of the steel sheet by hot rolling, to hot-band annealing with a hot-band annealing equipment provided with a heating zone, a soaking zone, a cooling zone, and a rapid heating device at an upstream side of the heating zone and/or in an inlet side of the heating zone, wherein the hot rolled steel sheet is heated by not lower than 50° C. at a heating rate of not less than 15° C./s by using the rapid heating device to improve a descaling property. Also, provided is a descaling method characterized by subjecting the Si-containing hot rolled steel sheet, after the hot-band annealing, to descaling only by pickling without requiring mechanical descaling or heating the steel sheet in the pickling process. 1. A hot-band annealing method comprising: (i) a rapid heating device is disposed at an upper stream side of the heating zone and/or an inlet side of the heating zone, and', '(ii) a start temperature for heating the Si-containing hot-rolled steel sheet in the rapid heating device is in a range of room temperature to 700° C. and the Si-containing hot rolled steel sheet is heated by not lower than 50° C. at a heating rate of not less than 15° C./s by using the rapid heating device., 'subjecting a Si-containing hot rolled steel sheet, having an oxidized scale formed on a surface of the steel sheet by hot rolling, to hot-band annealing with a hot-band annealing equipment provided with a heating zone, a soaking zone and a cooling zone, characterized in that'}2. The hot-band annealing method according to claim 1 , wherein the rapid heating device is an induction heating device or an electric heating device.3. A descaling method claim 1 , characterized by subjecting the Si-containing hot rolled steel sheet claim 1 , after the hot-band annealing by the method according to claim 1 , to pickling without conducting mechanical descaling.4. A ...

700MPA-Level High-Strength Hot Rolling Q&P Steel And Method Of Manufacturing The Same

A 700 Mpa-level high-strength hot rolling Q&P steel and the method of manufacturing the same, which steel has the chemical compositions in weight percentage as follows: C: 0.15%˜0.40%; Si: 1.0%˜2.0%; Mn: 1.5%˜3.0%; P: less than or equal to 0.015%; S: less than or equal to 0.005%; Al: 0.3%˜1.0%; N: less than or equal to 0.006%; Ti: 0.005%˜0.015%, the remainders being Fe; it having a yield strength of more than or equal to 700 Mpa, a tensile strength of more than or equal to 1300 Mpa and an elongation rate of more than 10%. Through reasonable design on the compositions and on the basis of the compositions of common C—Mn steel, the present invention improves the content of Si to restrict the precipitation of cementite, performs the micro-Ti treatment to refine the austenite grains, and improves the content of Al to quicken the austenite transformation dynamics during the air cooling process; at the same time, combines the hot rolling process with the staged cooling process to obtain the structures of proeutectoid ferrite plus martensite plus retained austenite and reduces the cost of alloy elements substantially.

Thick steel sheet having excellent ctod properties in multilayer welded joints, and manufacturing method for thick steel sheet

There is provided a thick steel plate having good multipass weld joint CTOD characteristics for low to medium heat input and a method for manufacturing the thick steel plate. A steel plate containing, on a mass percent basis, C: 0.03% to 0.12%, Si: 0.5% or less, Mn: 1.0% to 2.0%, P: 0.015% or less, S: 0.0005% to 0.0050%, Al: 0.005% to 0.060%, Ni: 0.5% to 2.0%, Ti: 0.005% to 0.030%, N: 0.0015% to 0.0065%, O: 0.0010% to 0.0050%, Ca: 0.0005% to 0.0060%, and optionally one or two or more of Cu and the like, wherein Ti/N, Ceq, Pcm, and ACR are in particular ranges, a base material of the plate has an effective grain size of 20 μm or less at half the thickness of the plate, and the plate contains a particular number of complex inclusions at ¼ and ½ of the thickness of the plate, the complex inclusions being composed of a sulfide containing Ca and Mn and an oxide containing Al and having an equivalent circular diameter of 0.1 μm or more. Steel having the composition described above is heated at a particular temperature, is then hot-rolled, and is cooled.

GRADIENT STEEL MATERIAL HAVING HIGH-PLASTICITY SURFACE LAYER AND HIGH-STRENGTH INNER LAYER, AND MANUFACTURING METHOD

A gradient steel material with a high plastic surface layer and a high strength inner layer, and a manufacturing method are provided. Weight percentages of the components of the gradient steel material are: C≤0.15%, Si≤1%, Mn≤1.5%, and the balance of Fe and inevitable impurities, the surface layer of the steel material being ferrite, and the inner layer being ferrite+bainite. The manufacturing method therefor comprises: smelting, casting, rolling, and a heat treatment, wherein in the heat treatment step, a steel material is heated to an austenite temperature Ac3 or more and kept at said temperature for more than 3 min; thereafter, the material is cooled to a temperature range between Ar3 and Ar1 in a two-phase zone at a cooling rate of less than 0.5° C./s, and is then cooled to room temperature at a cooling rate of greater than 5° C./s. The present steel material does not need to be obtained by means of the compound preparation of different materials as only a single material is processed. At the same time, the composition of the steel material is simple. Although the internal and external microstructures are different, the difference is a gradual process, and the strength at the interface is good. 1. A gradient steel material having a high-plasticity surface layer and a high-strength inner layer , comprising the following components in percentage by weight: 0 Подробнее

METHOD FOR HEAT TREATMENT OF A METAL COMPONENT

The invention relates to a method for heat treating a metal component. The invention relates in particular to an application in the partial hardening of optionally pre-coated components made of high-strength manganese-boron steel. With the method, at least one first sub-region of the component is convectively cooled by means of at least one nozzle, which discharges a fluid stream to the first sub-region so that a temperature difference of at least 100 K is set between the at least one first sub-region and at least one second sub-region of the component, wherein the at least one nozzle is operated with a positive pressure of at least 2 bar. 1. A method for heat treating a metal component , wherein the method comprising: convectively cooling at least one first sub-region of the component by means of at least one nozzle discharging a fluid stream toward the first sub-region , so that a temperature difference of at least 100 K is set between the at least one first sub-region and at least one second sub-region of the component , the at least one nozzle being operated at a positive pressure of at least 2 bar.2. The method according to claim 1 , further comprising claim 1 , prior to cooling claim 1 , heating at least the at least one first sub-region of the component by at least 500 K.3. The method according to claim 1 , further comprising claim 1 , after cooling claim 1 , heating at least the at least one first sub-region of the component by at least 100 K.4. A method for heat treating a metal component claim 1 , comprising at least the following steps:a) heating the component in a first furnace;b) moving the component into a temperature control station;c) convectively cooling at least one first sub-region of the component in the temperature control station by means of at least one nozzle discharging a fluid stream toward the first sub-region, wherein a temperature difference is set between the at least one first sub-region and at least one second sub-region of the ...

Selective Grain Boundary Engineering

A process for grain boundary engineering of an aluminum alloy of AA5XXX series which includes steps of annealing the aluminum alloy at a first temperature of from about 350° C. to about 450° C.; deforming the annealed aluminum alloy to reduce the thickness by from about 2% to about 20% of the original thickness of the aluminum alloy; heat treating the deformed aluminum alloy at a second temperature from about 450° C. to about 550° C., and optionally sensitizing the heat treated alloy in one or more sensitizing steps. Aluminum alloys of the AA5XXX series treated by the process of the present invention are also provided. 1. A process for grain boundary engineering of an aluminum alloy of AA5XXX series , said process comprising steps of:annealing said aluminum alloy at a temperature of from about 350° C. to about 450° C.;deforming said annealed aluminum alloy to reduce the thickness by from about 2% to about 20% of the original thickness of the aluminum alloy; andheat treating said deformed aluminum alloy at a temperature of from about 450° C. to about 550° C.2. The process of claim 1 , wherein said temperature in said annealing step is from about 370° C. to about 430° C.3. The process of claim 1 , wherein said annealing step is performed for a period from about 0.5 to about 3 hours.4. The process of claim 1 , further comprising the step of cooling the annealed aluminum alloy before the deforming step.5. The process of claim 4 , wherein said cooling step has a cooling rate of from about 10 to about 30° C. per minute.6. The process of claim 1 , wherein said deforming step comprises cold rolling.7. The process of claim 6 , wherein said cold rolling reduces the thickness from 3% to 15%.8. The process of claim 6 , wherein said cold rolling reduces the thickness from 5% to 10%.9. The process of claim 6 , wherein said cold rolling is performed at room temperature.10. The process of claim 1 , wherein said temperature in said heat treating step is from 475° C. to 525° C.11. ...

Heat treatment method and heat treatment device

The invention relates to a method and to a device for the heat treatment of a steel component directed specifically at individual zones of the component. In one or more first regions of the steel component a primarily austenitic structure can be set, from which, by quenching, a predominantly martensitic structure can be produced, and in one or more second regions of the steel component there is a predominantly ferritic-pearlitic structure. The steel component is first of all heated in a first furnace to a temperature below the Ac3 temperature, and the steel component is then transferred into a handling station. During the transfer the steel component can cool, and in the handling station, one or more second regions of the steel component are cooled within a residence time t150 to a final cooling temperature ϑS, and is then transferred to a second furnace, in which heat is delivered to the steel component. The temperature of the one or more second regions increases again during the residence time t130 to a temperature below the Ac3 temperature, whilst the temperature of the one or more first regions is heated in the same residence time t130 to a temperature above the Ac3 temperature.

CARBIDE-FREE BAINITE AND RETAINED AUSTENITE STEELS, PRODUCING METHOD AND APPLICATIONS OF SAME

One aspect, this invention relates to a carbide-free bainite and retained austenite steel including a composition designed and processed such that the carbide-free bainite and retained austenite steel meets property objectives comprising a yield strength in a range of about 1000-2000 MPa, a uniform ductility, a desired total elongation and hole-expansion ratio, a desired level of weldability and an austenite stability designed to have an austenite start temperature M to be equal to an application temperature in range from about 50° C. to −50° C. The property objectives are design specifications of the carbide-free bainite and retained austenite steel. 1. A carbide-free bainite and retained austenite steel , comprising:{'sub': 's', 'sup': 'σ', 'a composition designed and processed such that the carbide-free bainite and retained austenite steel meets property objectives comprising a yield strength in a range of about 1000-2000 MPa, a uniform ductility, a desired total elongation and hole-expansion ratio, a desired level of weldability and an austenite stability designed to have an austenite start temperature M to be equal to an application temperature in range from about 50° C. to −50° C., wherein the property objectives are design specifications of the carbide-free bainite and retained austenite steel.'}2. The carbide-free bainite and retained austenite steel of claim 1 , wherein the composition is processed with a cooling and partitioning treatment.3. The carbide-free bainite and retained austenite steel of claim 1 , wherein the composition comprises carbon (C) no more than 0.4 wt % claim 1 , silicon (Si) no less than 1.0 wt % claim 1 , and iron (Fe) in balance.4. The carbide-free bainite and retained austenite steel of claim 2 , wherein the composition further comprises manganese (Mn) in a range of about 0.2-1.0 wt. % claim 2 , and molybdenum (Mo) in a range of about 0.4-0.8 wt. %.5. The carbide-free bainite and retained austenite steel of claim 2 , wherein the ...

High strength hot-rolled steel sheet having excellent workability, and method for manufacturing the same

Provided is a steel material that may be used for arms, frames, beams, brackets, reinforcing materials, etc. of chassis parts of a vehicle and, more specifically, to a high strength hot-rolled steel sheet having excellent workability and a method for manufacturing same. The steel sheet includes: by weight %, 0.1-0.15% of C, 2.0-3.0% of Si, 0.8-1.5% of Mn, 0.001-0.05% of P, 0.001-0.01% of S, 0.01-0.1% of Al, 0.7-1.7% of Cr, 0.0001-0.2% of Mo, 0.02-0.1% of Ti, 0.01-0.03% of Nb, 0.001-0.005% of B, 0.1-0.3% of V, 0.001-0.01% of N, and a balance of Fe and inevitable impurities, wherein tensile strength (TS) is 1180 MPa or more, a product (TS×E1) of tensile strength and elongation is 20,000 MPa % or more, and a product (TS×HER) of tensile strength and hole expandability is 30,000 MPa % or more.

Ni-Based Alloy Product and Method for Producing Same, and Ni-Based Alloy Member and Method for Producing Same

There are provided: an Ni-based alloy member including a γ′ phase precipitation with 36 to 60 volume % and exhibiting a high durable temperature and good cold workability; a method for producing the member; an Ni-based alloy product to be used as a precursor of the member; and a method for producing the product. The Ni-based alloy product has a two-phase structure composed of a γ phase and a γ′ phase being incoherent to the γ phase, the incoherent γ′ phase being present at a ratio of 20 volume % or higher. The Ni-based alloy member produced by cold working the Ni-based alloy product and subsequently by conducting heat treatment comprises a γ phase and a γ′ phase being coherent to the γ phase, the coherent γ′ phase being present at a ratio of 36 to 60 volume %, and has a predetermined shape. 1. A method for producing an Ni-based alloy product having a two-phase structure composed of crystalline grains of a γ phase and crystalline grains of the γ′ phase , in which the γ′ phase is an incoherent γ′ phase being located through γ phase grain boundaries of an incoherent interface , and in which the incoherent γ′ phase is present at a ratio of 20 volume % or higher in the two-phase structure , the method comprising:the step of melting and casting a first Ni-based alloy material to produce a second Ni-based alloy material; andthe step of hot-forging the second Ni-based alloy material obtained through the melting and casting step at temperatures equal to or higher than 1000° C. and wherein the γ and the γ′ phases coexist to produce a third Ni-based alloy material having an ingredient composition in which a γ′ phase at a ratio of 36 to 60 volume % can be precipitated in a temperature range of 700 to 900° C.; andthe step of forming the Ni-based alloy product from the third Ni-based alloy material.2. The method for producing an Ni-based alloy product according to claim 1 ,wherein the γ′ phase precipitates at a ratio of 10 volume % or higher in the hot-forging step.3. The method ...

Hot steel forging in horizontal press

The present disclosure relates to a steel forging process, in particular a hot steel forging process in horizontal press of a metal tube, preferably a cylindrical steel tube.

STEEL SHEET AND METHOD FOR PRODUCING SAME

Disclosed herein are a steel sheet having excellent aging resistance and low yield ratio properties, and a method for producing the same. The disclosed sheet comprises, by weight, 0.005-0.06% carbon (C), 0.2% or less silicon (Si), 1.0-2.0% manganese (Mn), 0.08% or less phosphorus (P), 0.01% or less sulfur (S), 0.2-2.0% aluminum (Al), one or more of chromium (Cr) and molybdenum (Mo) in an amount satisfying 0.3≦[Cr wt %]+0.3[Mo wt %]≦2.0, and 0.008% or less nitrogen (N), with the remainder being iron (Fe) and inevitable impurities, and has a single-phase structure of ferrite in a hot-rolled state, and a two-phase structure of ferrite and martensite in a cold-rolled state. 1. A steel sheet comprising by weight: 0.005-0.06% carbon (C) , 0.2% or less silicon (Si) , 1.0-2.0% manganese (Mn) , 0.08% or less phosphorus (P) , 0.01% or less sulfur (S) , 0.2-2.0% aluminum (Al) , one or more of chromium (Cr) and molybdenum (Mo) in an amount satisfying 0.3≦[Cr wt %]+0.3[Mo wt %]≦2.0 , and 0.008% or less nitrogen (N) , with a remainder being iron (Fe) and inevitable impurities , the steel sheet having a single-phase structure of ferrite in a hot-rolled state and having a two-phase structure of ferrite and martensite in a cold-rolled state.2. The steel sheet of claim 1 , wherein the phosphorous (P) is 0.02-0.08 wt %.3. The steel sheet of claim 1 , wherein the [Cr wt %]+0.3[Mo wt %] is 0.5-1.5.4. The steel sheet of claim 1 , wherein the chromium (Cr) is 0.3-1.5 wt % chromium (Cr).5. The steel sheet of claim 4 , wherein one or more of phosphorous (P) is 0.02-0.08 wt % and molybdenum (Mo) is 0.05-0.4 wt % molybdenum (Mo).6. The steel sheet of claim 1 , wherein aluminum (Al) is 0.3-1.0 wt %.7. The steel sheet of claim 1 , further comprising 5.0-10.0% by area of martensite with a remainder being ferrite claim 1 , in the cold-rolled state.8. The steel sheet of claim 7 , further comprising a density of dislocations in a ferrite matrix of the steel sheet in the cold-rolled state is 1×10/ ...

FERRITIC STAINLESS STEEL SHEET WHICH IS EXCELLENT IN WORKABILITY AND METHOD OF PRODUCTION OF SAME

Ferritic stainless steel sheet which is excellent in ridging resistance which comprises, by mass %, Cr: 10 to 30%, Sn: 0.005 to 1%, C: 0.001 to 0.1%, N: 0.001 to 0.1%, Si: 0.01 to 3.0%, Mn: 0.01 to 3.0%, P: 0.005 to 0.1%, and S: 0.0001 to 0.01% and has a balance of Fe and unavoidable impurities and which has an X-ray diffraction strength in the {100}<012> orientation from a surface layer to t/4 (“t” is sheet thickness) of 2 or more. 1. A method of producing a ferritic stainless steel sheet excellent in workability comprising , by mass % , Cr: 10 to 30% , Sn: 0.005 to 1% , C: 0.001 to 0.1% , N: 0.001 to 0.1% , Si: 0.01 to 3.0% , Mn: 0.01 to 3.0% , P: 0.005 to 0.1% , S: 0.0001 to 0.01% and a balance of Fe and unavoidable impurities ,wherein an X-ray diffraction strength in the {100}<012> orientation from a surface layer of the steel Sheet to t/4 is 2 or More, Wherein “t” Represents the sheet thickness,the method comprising the steps of:heating a hot rolled steel sheet to 850° C. during annealing the steel sheet;cooling the steel sheet down to 500° C. by a cooling speed of over 10° C./sec and less than 15° C./sec; andcold rolling the steel sheet using rolls of a diameter of 150 mm or less by a reduction rate of 60% or more.2. A method of producing a ferritic stainless steel sheet excellent in workability comprising , by mass % , Cr: 10 to 30% , Sn: 0.005 to 1% , C: 0.001 to 0.1% , N: 0.001 to 0.1% , Si: 0.01 to 3.0% , Mn: 0.01 to 3.0% , P: 0.005 to 0.1% , S: 0.0001 to 0.01% , and further comprising , by mass % , one or more of Ti: 0.005 to 0.5% , Nb: 0.005 to 0.5% , Zr: 0.005 to 0.5% , V: 0.01 to 0.5% , Ni: 0.01 to 1% , Mo: 0.1 to 3.0% , W: 0.1 to 3.0% , Cu: 0.1 to 3.0% , B: 0.0003 to 0.0100% , Al: 0.01 to 1.0% , Ca: 0.0001 to 0.003% , Mg: 0.0001 to 0.005% , Co: 0.001 to 0.5% , Sb: 0.005 to 0.3% , REM: 0.001 to 0.2% , and Ga: 0.0002 to 0.3% or less and a balance of Fe and unavoidable impurities ,wherein an X-ray diffraction strength in the {100}<012> orientation from a ...

HIGH STRENGTH HOT ROLLED STEEL SHEET AND METHOD FOR MANUFACTURING THE SAME (AS AMENDED)

A high strength hot rolled steel sheet having a tensile strength TS of 980 MPa or more, has a composition containing, on a percent by mass basis, C: 0.05% or more and 0.18% or less, Si: 1.0% or less, Mn: 1.0% or more and 3.5% or less, P: 0.04% or less, S: 0.006% or less, Al: 0.10% or less, N: 0.008% or less, Ti: 0.05% or more and 0.20% or less, V: more than 0.1% and 0.3% or less, and the balance being Fe and incidental impurities, and has a microstructure including a primary phase and a secondary phase, the primary phase being a bainite phase having an area fraction of more than 85%, the secondary phase being at least one of ferrite phase, martensite phase, and retained austenite phase, the secondary phase having an area fraction of 0% or more and less than 15% in total, the bainite phase having an average lath interval of laths of 400 nm or less, and the laths having an average long axis length of 5.0 μm or less. 1. A high strength hot rolled steel sheet having a tensile strength TS of 980 MPa or more , comprising a composition and a microstructure ,the composition containing, on a percent by mass basis,C: 0.05% or more and 0.18% or less, Si: 1.0% or less,Mn: 1.0% or more and 3.5% or less, P: 0.04% or less,S: 0.006% or less, Al: 0.10% or less,N: 0.008% or less, Ti: 0.05% or more and 0.20% or less,V: more than 0.1% and 0.3% or less, andthe balance being Fe and incidental impurities, andthe microstructure comprising a primary phase and a secondary phase,the primary phase being a bainite phase having an area fraction of more than 85%,the secondary phase being at least one of ferrite phase, martensite phase, and retained austenite phase, the secondary phase having an area fraction of 0% or more and less than 15% in total,the bainite phase having an average lath interval of laths of 400 nm or less, and the laths having an average long axis length of 5.0 μm or less.2. The high strength hot rolled steel sheet according to claim 1 , wherein the composition further contains ...

Grain-oriented electrical steel sheet and method for manufacturing the same

A grain-oriented electrical steel sheet includes a base steel sheet which contains Si and Mn, an intermediate layer which is disposed on a surface of the base steel sheet and contains a silicon oxide as a main component, and an insulation coating which is disposed on a surface of the intermediate layer. A final-annealed film is not substantially present on a surface of the base steel sheet. In a surface layer region of grain-oriented electrical steel sheet, a Mn-depletion layer having a valley portion of a Mn content in which a Mn content is lower than an average Mn content of the base steel sheet in a region deeper than the surface layer region is provided, and a Mn-rich layer having a peak portion of a Mn content in which a Mn content is higher than that in the valley portion of the Mn content is provided in a region closer to a surface of the insulation coating than the Mn-depletion layer.

GALVANNEALED STEEL SHEET AND MANUFACTURING METHOD THEREOF

A galvannealed steel sheet excellent in press formability including a plating layer being a plating layer containing 7.2 to 10.6 mass % of Fe, 0.2 to 0.4 mass % of Al, and 0.1 mass % of Ni and the like, and the balance being composed of Zn and impurities, in which in a vertical cross-section of the plating layer, an average thickness of a ξ phase is 0.2 μm or less and an average thickness of Γ phases existing in contact with a base iron is 0.5 μm or less, in the Γ phase, Ni and the like are contained at a ratio in the Γ phase of 0.5 mass % or more, a phase existing in contact with the Γ phase is a mixed phase of Γphase and δ phase, and a δ phase percentage defined by Expression below is 10% or more. δ phase percentage=(δ phase/Γ phase contact interface length)/(δ phase/Γ phase contact interface length+Γphase/Γ phase contact interface length)×100 Here, the δ phase/Γ phase contact interface length is the length of the interface at which the δ phase and the Γ phase are in contact, and the Γphase/Γ phase contact interface length is the length of the interface at which the Γphase and the Γ phase are in contact. 1. A galvannealed steel sheet , comprising:a base iron; anda plating layer containing 7.2 to 10.6 mass % of Fe, 0.2 to 0.4 mass % of Al, and 0.1 mass % or more in total of one type or more types selected from the group consisting of Ni, Co, Cu, and In, and the balance being composed of Zn and impurities, whereinthe plating layer is formed on a surface of the base iron, whereinin a vertical cross-section of the plating layer, an average thickness of a ξ phase is 0.2 μm or less, and an average thickness of Γ phases existing in contact with the base iron is 0.5 μm or less, whereinin the Γ phase, the one type or more types selected from the group consisting of Ni, Co, Cu, and In are contained 0.5 mass % or more in total in the Γ phase, and wherein{'sub': '1', 'claim-text': {'br': None, 'sub': '1', 'δ phase percentage=(δ phase/Γ phase contact interface length)/(δ phase ...

METHOD OF FORMING GOLF CLUB HEAD ASSEMBLY

A method of forming a golf club head assembly includes aligning a faceplate with a recess of a club head; welding the faceplate to the club head; then, after welding the faceplate, heating the club head and the faceplate to at least a solvus temperature of the faceplate for a predetermined amount of time; and then, after heating the club head and the faceplate, allowing the club head and the faceplate to air cool. 262. The method of claim 1 , wherein the α- titanium alloy comprising between 6.5 wt % to 10 wt % aluminum.362. The method of claim 1 , wherein the α- titanium alloy further comprises 1.0 wt % to 2.0 wt % vanadium (V) claim 1 , 0.20 wt % or less oxygen (O) claim 1 , and 0.20 wt % or less silicon (Si).462. The method of claim 3 , wherein the α- titanium alloy further comprises 0.30 wt % or less iron (Fe) claim 3 , 0.08 wt % or less carbon (C) claim 3 , 0.05 wt % or less nitrogen (N) claim 3 , trace molybdenum (Mo) claim 3 , trace tin (Sn) claim 3 , and the remaining weight percent is titanium (Ti).5. The method of claim 1 , wherein the welding of step (c) includes a pulse plasma welding process.6. The method of claim 1 , wherein the inert gas of step (e) is selected from the group consisting of nitrogen (N) claim 1 , argon (Ar) claim 1 , helium (He) claim 1 , neon (Ne) claim 1 , krypton (Kr) claim 1 , and xenon (Xe) or a compound gas thereof.7. The method of claim 6 , wherein the inert gas is nitrogen (N) or argon (Ar).8. The method of claim 1 , wherein the faceplate of step (a) has a minimum thickness of 0.7 mm.9. The method of claim 1 , wherein step (d) includes heating the club head and the faceplate between 550° C. and 625° C. for between 1 hour and 2 hours.10. The method of claim 9 , wherein heating the club head and the faceplate includes heating the club head and the faceplate to between 575° C. and 625° C. for between 1 hour and 2 hours.12. The method of claim 11 , wherein the faceplate remains within 10% of its original bulge and roll curvature ...

HEAT-TREATED STEEL MATERIAL AND METHOD OF MANUFACTURING THE SAME

A heat-treated steel material includes: a chemical composition expressed by, in mass %: C: 0.16% to 0.38%; Mn: 0.6% to 1.5%; Cr: 0.4% to 2.0%; Ti: 0.01% to 0.10%; B: 0.001% to 0.010%; Si: 0.20% or less; P: 0.05% or less; S: 0.05% or less; N: 0.01% or less; Ni: 0% to 2.0%; Cu: 0% to 1.0%; Mo: 0% to 1.0%; V: 0% to 1.0%; Al: 0% to 1.0%; Nb: 0% to 1.0%; REM: 0% to 0.1%; and the balance: Fe and impurities; and a structure expressed by: retained austenite: 1.5 volume % or less; and the balance: martensite. 1. A heat-treated steel material comprising: C: 0.16% to 0.38%;', 'Mn: 0.6% to 1.5%;', 'Cr: 0.4% to 2.0%;', 'Ti: 0.01% to 0.10%;', 'B: 0.001% to 0.010%;', 'Si: 0.20% or less;', 'P: 0.05% or less;', 'S: 0.05% or less;', 'N: 0.01% or less;', 'Ni: 0% to 2.0%;', 'Cu: 0% to 1.0%;', 'Mo: 0% to 1.0%;', 'V: 0% to 1:0%;', 'Al: 0% to 1.0%;', 'Nb: 0% to 1.0%;', 'REM: 0% to 0.1%; and', 'the balance: Fe and impurities; and, 'a chemical composition expressed by, in mass % retained austenite: 1.5 volume % or less; and', 'the balance: martensite., 'a structure expressed by2. The heat-treated steel material according to claim 1 , wherein C: 0.16 to 0.25% in the chemical composition.3. The heat-treated steel material according to claim 1 , comprising a mechanical property expressed bya yield ratio: 0.70 or more.4. The heat-treated steel material according to claim 1 , wherein the chemical composition satisfies:Ni: 0.1% to 2.0%;Cu: 0.1% to 1.0%;Mo: 0.1% to 1.0%;V: 0.1% to 1.0%;Al: 0.01% to 1.0%;Nb: 0.01% to 1.0%; orREM: 0.001% to 0.1%; orany combination thereof.5. A method of manufacturing a heat-treated steel material claim 1 , comprising:{'sub': '3', 'heating a steel sheet to a temperature of an Acpoint or higher;'}next cooling the steel sheet to a Ms point at a cooling rate equal to a critical cooling rate or more; andnext cooling the steel sheet from the Ms point to 100° C. at a 35° C./second average cooling rate or more, whereinthe steel sheet comprises a chemical composition ...

Production Method for Plated Steel Sheet Using a Steel Sheet Annealing Device

Provided is a method for producing plated steel sheet by means of an annealing device which includes at least one section and in which the at least one section is filled with a gas constituting a non-reducing atmosphere or a weakly reducing atmosphere to substantially improve the quality of plating onto hot-dipped steel sheet, including the plating properties, alloying properties, anti-pickup properties, plating adhesion properties, anti-flaking properties, anti-cratering properties and anti-ash properties, by using prior-art annealing equipment and heat-treatment cycle without any additional oxidation-reduction heat treatment process or large quantities of high-cost alloying elements. 1. A plated steel sheet manufacturing method including:performing a series of processes for manufacturing a plated steel sheet by performing an annealing process on a steel sheet in an annealing device,the annealing device including at least one section, and the annealing process being performed in the at least one section containing a gas constituting a non-reducing atmosphere or a weakly reducing atmosphere.2. The method of claim 1 , wherein the annealing process includes at least one operation selected from the group consisting of pre heating claim 1 , heating claim 1 , soaking claim 1 , slow cooling claim 1 , rapid cooling claim 1 , and final cooling.3. The method of claim 2 , wherein the annealing process further includes at least one of overaging and re-heating operations.4. The method of claim 2 , wherein the pre heating operation or the heating operation is an induction heating scheme claim 2 , an infrared heating scheme claim 2 , a radiant tube burning scheme claim 2 , an ultrasonic wave burning scheme claim 2 , or a scheme having a combination thereof.5. The method of claim 3 , wherein the re-heating operation is an induction heating scheme claim 3 , an infrared heating scheme claim 3 , a radiant tube burning scheme claim 3 , an ultrasonic wave burning scheme claim 3 , or a ...

Method and apparatus for supercooling of metal/alloy melts and for the formation of amorphous metals therefrom

A method and apparatus is described for creation of amorphous metals using electromagnetic supercooling of a metal/alloy without the utilization of rapid quenching nor immaculate process environments. By exposing the cooling melt to electric currents, either induced by an alternating magnetic field or supplied directly, crystallization is suppressed and the melt can reach significant levels of supercooling. With sufficient current densities in the melt the supercooling can extend all the way into the glass transition range for certain materials at which point an amorphous metal/alloy is created.

High-formability and super-strength hot galvanizing steel plate and manufacturing method thereof

A high-formability, super-high-strength, hot-dip galvanized steel plate, the chemical composition of which comprises, based on weight percentage, C: 0.15-0.25 wt %, Si: 1.00-2.00 wt %, Mn: 1.50-3.00 wt %, P≦0.015 wt %, S≦0.012 wt %, Al: 0.03-0.06 wt %, N≦0.008 wt %, and the balance of iron and unavoidable impurities. The room temperature structure of the steel plate comprises 10-30% ferrite, 60-80% martensite and 5-15% residual austenite. The steel plate has a yield strength of 600-900 MPa, a tensile strength of 980-1200 MPa, and an elongation of 15-22%. Through an appropriate composition design, a super-high-strength, cold rolled, hot-dip galvanized steel plate is manufactured by continuous annealing, wherein no expensive alloy elements are added; instead, remarkable increase of strength along with good plasticity can be realized just by appropriate augment of Si, Mn contents in combination with suitable processes of annealing and furnace atmosphere control. In addition, the steel plate possesses good galvanization quality that meets the requirement of a super-high-strength, cold rolled, hot-dip galvanized steel plate for automobiles.

VERY HIGH-STRENGTH, COLD-ROLLED, DUAL STEEL SHEETS

The present invention provides a cold-rolled and annealed Dual-Phase steel sheet having a tensile strength from 980 to 1100 MPa. The composition includes the contents being expressed by weight: 0.055%≤C≤0.095%, 2%≤Mn≤2.6%, 0.005%≤Si≤0.35%, S≤0.005%, P≤0.050%, 0.1≤Al≤0.3%, 0.05%≤Mo≤0.25%, 0.2%≤Cr≤0.5%, Cr+2 Mo≤0.6%, Ni≤0.1%, 0.010≤Nb≤0.040%, 0.010≤Ti≤0.050%, 0.0005≤B≤0.0025%, and 0.002%≤N≤0.007%. The remainder of the composition includes iron and inevitable impurities resulting from the smelting. A microstructure of the steel sheet is 40 to 65% ferrite, 35 to 50% martensite and 0 to 10% bainite. A non-recrystallized ferrite fraction is less than or equal to 15%. 1. A cold-rolled and annealed Dual-Phase steel sheet comprising: 0.055%≤C≤0.095%;', '2%≤Mn≤2.6%;', '0.005%≤Si≤0.35%;', 'S≤0.005%;', 'P≤0.050%;', '0.1≤Al≤0.3%;', '0.05%≤Mo≤0.25%;', '0.2%≤Cr≤0.5%;', 'Cr+2Mo≤0.6%;', 'Ni≤0.1%;', '0.010≤Nb≤0.040%;', '0.010≤Ti≤0.050%;', '0.0005≤B≤0.0025%; and', '0.002% ≤N≤0.007%;', 'a remainder of the composition comprising iron and the inevitable impurities resulting from smelting;, 'a composition comprising, the contents being expressed by weighta tensile strength between 980 and 1100 MPa; anda microstructure consisting of 40 to 65% ferrite, 35 to 50% martensite and 0 to 10% bainite, a non-recrystallized ferrite fraction being less than or equal to 15%.2. The steel sheet as recited in claim 1 , wherein the composition of the steel contains claim 1 , the content being expressed by weight: 0.12%≤Al≤0.25%.3. The steel sheet as recited in claim 1 , wherein the composition of the steel contains claim 1 , the content being expressed by weight: 0.10%≤Si≤0.30%.4. The steel sheet as recited in claim 1 , wherein the composition of the steel contains claim 1 , the content being expressed by weight: 0.15%≤Si≤0.28%.5. The steel sheet as recited in claim 1 , wherein the composition of the steel contains claim 1 , the content being expressed by weight: P≤0.015%.6. The steel sheet as recited in ...

HT550 STEEL PLATE WITH ULTRAHIGH TOUGHNESS AND EXCELLENT WELDABILITY AND MANUFACTURING METHOD OF THE SAME

An HT550 steel plate with ultrahigh toughness and excellent weldability and a manufacturing method thereof are disclosed. Based on a component system with ultralow-C, high-Mn, Nb-microalloying, ultramicro Ti treatment, Mn/C is controlled in the range of 15˜30, (% Si)×(% Ceq) is less than or equal to 0.050, (% C)×(% Si) is less than or equal to 0.010, (% Mo)×[(% C)+0.13(% Si)] is in the range of 0.003˜0.020, the ratio Ti/N is in the range of 2.0˜4.0, the steel plate is alloyed with (Cu+Ni+Mo), Ni/Cu is greater than or equal to 1.0, Ca treatment is performed, and Ca/S is in the range of 0.80˜3.00; by optimizing TMCP process, the steel plate has microstructures of fine ferrite plus self-tempered bainite with an average grain size being less than or equal to 15 μm, yield strength being 460 MPa or more, tensile strength being 550˜700 MPa, yield ratio being 0.85 or less, and −60° C. Charpy impact energy (single value) being 60 J or more; therefore, the steel plate is capable of bearing large thermal input welding while obtaining uniform and excellent strength, toughness, and strong plasticity matching, and is especially suitable for sea bridge structures, ocean wind tower structures, ocean platform structures and hydroelectric structures. 1. An HT550 steel plate with ultrahigh toughness and excellent weldability , having the following components in weight percentage:C: 0.04%˜0.09%;Si: less than 0.15%;Mn: 1.25%˜1.55%;P: less than 0.013%;S: less than 0.003%;Cu: 0.10%˜0.30%;Ni: 0.20%˜0.60%;Mo: 0.05%˜0.25%;Als: 0.030%˜0.060%;Ti: 0.006%˜0.014%;Nb: 0.015%˜0.030%;N: less than 0.0050%;Ca: 0.001%˜0.004%;the remaining being Fe and inevitable impurities;and simultaneously, the contents of the above-described elements meeting the following relationships:the relationship between C and Mn: the ratio Mn/C is more than or equal to 15 and less than or equal to 30;(% Si)×(% Ceq) is less than or equal to 0.050, wherein Ceq=C+Mn/6+(Cu+Ni)/15+(Cr+Mo+V)/5;(% Si)×(% C) is less than or equal to ...

Hot rolled coated steel sheet having high strength, high formability, excellent bake hardenability and method of manfuacturing same

A hot-rolled coated steel sheet including: in wt %, C: 0.05-0.14%, Si: 0.1-1.0%, Mn: 1.0-2.0%, P: 0.001-0.05%, S: 0.001-0.01%, AI: 0.01-0.1%, Cr: 0.005-1.0%, Ti: 0.005-0.13%, Nb: 0.005-0.03%, N: 0.001-0.01%, Fe residues, and other inevitable impurities; a mixed structure of ferrite and bainite as a main phase; and as a remaining structure, one or more selected from the group consisting of martensite, austenite, and phase martensite (MA), wherein a fraction of the ferrite and bainite is 95-99 area % and Equation 1 is satisfied. [Equation 1] FCO{110}<112>+FCO{112}<111>≥10 where, FCO{110}<112> and FCO{112}<111>, each representing an area fraction occupied by a structure having ac crystal orientation of {110}<112> and {112}<111>.

METHOD OF MANUFACTURING CEMENTED CARBIDE CUTTING TOOL AND CUTTING TOOL MANUFACTURED BY THE METHOD

Method of manufacturing a cemented carbide cutting tool, includes a) bonding a body part of hot work tool steel and a cutting part of cemented carbides together by heat treatment; b) cooling the bonded body part and cutting part for a preset period of time; c) machining the cutting part to have a predetermined pattern according to its application and forming a cutting tool; d) coating a surface of the machined cutting tool with a film of at least one of metallic oxides, nitrides and carbides; and e) cooling the coated cutting tool for a preset period of time in air, and a cutting tool manufactured by the method. Cracks do not generate even after the coating step, and thus cemented carbide cutting tool having excellent mechanical properties may be manufactured. 1. A method of manufacturing a cemented carbide cutting tool , comprising:a) bonding a body part of hot work tool steel and a cutting part of cemented carbides together by heat treatment;b) cooling slowly the bonded body part and cutting part for 24 hours in a vacuum chamber;c) machining the cutting part to have a predetermined pattern according to its purpose and forming a cutting tool;d) coating a surface of the machined cutting tool with a film of at least one of a metallic oxide, a nitride and a carbide so as to enhance mechanical properties of the cutting tool; ande) cooling the coated cutting tool for a preset period of time in air.2. The method of claim 1 , wherein the hot work tool steel is SKD61 and the step a) comprises bonding the body part and the cutting part at a temperature of 800 to 1200° C. by high-frequency welding or oxygen welding.3. (canceled)4. The method of claim 1 , wherein the step c) comprises grinding the cutting part by a relief grinder so that a plurality of blades having the same cutting relief angle are formed of a curved shape in a circumferential direction of the cutting part.5. The method of claim 1 , wherein the step d) comprises depositing a titanium aluminum nitride (TiAlN) ...

Hot-pressed member and method for manufacturing same, and cold-rolled steel sheet for hot pressing and method for manufacturing same

Disclosed is a hot-pressed member that can exhibit very high tensile strength after hot pressing as high as TS: 1780 MPa or more, and excellent resistance to resistance welding cracking by properly adjusting its chemical composition and its microstructure such that a prior austenite average grain size is 7.5 μm or less, a volume fraction of martensite is 95% or more, and at least 10 Nb-based and Ti-based precipitates having a grain size of less than 0.10 μm are present on average per 100 μm 2 of a cross section parallel to a thickness direction of the member within a range of 100 μm or less in the thickness direction from the surface of the member, and such that a B concentration in prior austenite grain boundaries is at least 3.0 times a B concentration at a position 5 nm away from the grain boundaries.

PRODUCTION METHOD FOR ALLOY 690 ORDERED ALLOY OF IMPROVED THERMAL CONDUCTIVITY, AND ALLOY 690 ORDERED ALLOY PRODUCED THEREBY

The present invention relates to ordered Alloy 690 with improved thermal conductivity. By maintaining Alloy 690 in a temperature range of 350-570° C. for a proper amount of time, the atomic arrangement is controlled to properly form the ordered phases. The ordered phases formed in the ordered Alloy 690 increases its thermal conductivity due to a low thermal scattering effect of the ordered phase as observed in pure metals. 1. A method of manufacturing ordered Alloy 690 with improved thermal conductivity , the method comprising:solution-annealing Alloy 690;thermally treating the solution-annealed Alloy 690 to manufacture Alloy 690 TT; andordering the Alloy 690 TT by annealing in a temperature range of 350-570° C. to manufacture ordered Alloy 690.2. A method of manufacturing ordered Alloy 690 with improved thermal conductivity , the method comprising:solution-annealing Alloy 690;thermally treating the solution-annealed Alloy 690 to manufacture Alloy 690 TT; andordering the Alloy 690 TT by annealing in a temperature range of 350-570° C. before cooling the Alloy 690 TT to room temperature to manufacture ordered Alloy 690.3. A method of manufacturing ordered Alloy 690 with improved thermal conductivity , including the method where Alloy 690 TT is given the ordering treatment in a temperature range of 350-570° C.4. The method according to claim 1 , wherein the ordering treatment is performed on Alloy 690 TT in a temperature range of 400-510° C.5. The method according to claim 1 , wherein the thermal conductivity increase rate of the ordered Alloy 690 is 8% or more claim 1 , as compared to before the ordering treatment.6. The method according to claim 4 , wherein the thermal conductivity increase rate of the ordered Alloy 690 is 8% or more claim 4 , as compared to before the ordering treatment.7. The method according to claim 5 , wherein the ordering treatment is performed in a process of cooling at a rate of 1° C./min or lower.8. The method according to claim 6 , wherein ...

Pre-weld heat treatment for a nickel based superalloy

A pre-weld heat treatment of the nickel based superalloy including heating a nickel based superalloy (e.g., IN939) casting to 2120° F. at a rate of 2° F. per minute, and then soaking the casing for one hour at 2120° F. The casting is then cooled in stages including slowly cooling the casting at a rate of 1° F. per minute to about 1900° F. and holding at that temperature for about 10 minutes. Then the casting is further slowly cooled at a rate of 1° F. per minute to about 1800° F. and holding at that temperature for about 10 minutes, and further slowly cooled to a temperature range of 1650° F. to 1450° F., and then fast cooled to room temperature. The pre-weld heat treatment may optionally include a step of heating the casting to about 1850° F. at a rate of 50° F. per minute before slowly heating to 2120° F.

Ni-Based Alloy Product and Method for Producing Same, and Ni-Based Alloy Member and Method for Producing Same

There are provided: an Ni-based alloy member including a γ′ phase precipitation with 36 to 60 volume % and exhibiting a high durable temperature and good cold workability; a method for producing the member; an Ni-based alloy product to be used as a precursor of the member; and a method for producing the product. The Ni-based alloy product has a two-phase structure composed of a γ phase and a γ′ phase being incoherent to the γ phase, the incoherent γ′ phase being present at a ratio of 20 volume % or higher. The Ni-based alloy member produced by cold working the Ni-based alloy product and subsequently by conducting heat treatment comprises a γ phase and a γ′ phase being coherent to the γ phase, the coherent γ′ phase being present at a ratio of 36 to 60 volume %, and has a predetermined shape. 1. An Ni-based alloy product , having a two-phase structure composed of a γ (gamma) phase and a γ′ (gamma prime) phase that is incoherent with the γ phase ,wherein the γ′ phase is present at a ratio of 20 volume % or higher.2. The Ni-based alloy product according to claim 1 ,wherein each crystalline grain of the γ phase and the γ′ phase is 100 μm or smaller in grain size.3. An Ni-based alloy member produced through cold working and annealing of the Ni-based alloy product according to claim 1 , the Ni-based alloy member comprising a γ (gamma) phase and a γ′ (gamma prime) phase that is coherent with the γ phase claim 1 ,wherein the γ′ phase is present at a ratio of 36 to 60 volume %, andwherein the Ni-based alloy member has a predetermined shape.4. A method for producing an Ni-based alloy product claim 1 , the method comprising the step of hot-forging an Ni-alloy at temperatures equal to or higher than 1000° C. claim 1 ,wherein the Ni-based alloy product has a two-phase structure composed of a γ (gamma) phase and a γ′ (gamma prime) phase that is incoherent with the γ′ phase, andwherein the γ′ phase is present at a ratio of 20 volume % or higher.5. The method for producing an Ni- ...

LOW-CRACK-SENSITIVITY AND LOW-YIELD-RATIO ULTRA-THICK STEEL PLATE AND PREPARATION METHOD THEREFOR

An ultra-heavy steel plate with low cracking sensitivity and low yield ratio, the mass percentages of chemical components of the steel plate are C 0.05-0.09; Si 0.2-0.4; Mn 1.3-1.6; Al 0.02-0.04; Nb 0.03-0.08; V 0.03-0.08; Cr 0.1-0.5; Ni 0.1-0.5; Mo 0.1-0.3; Cu 0.2-0.5; Ti 0.01-0.02; P≤0.015; S≤0.003; N≤0.007, the balance being Fe and inevitable impurities; the carbon equivalent is ≤0.43, the cold cracking sensitivity coefficient Pcm is ≤0.20. A low cracking sensitivity and low yield ratio steel plate with a thickness of 40-70 mm is manufactured by the process steps of KR molten iron pretreatment-converter smelting-LF refining-RH vacuum degassing-continuous casting-lid-covering slow cooling for the continuous casting slabs-casting slabs heating-controlled rolling-controlled cooling-hot straightening-air cooling and so on. 1. An ultra-heavy steel plate with low cracking sensitivity and low yield ratio (i.e. ratio of yield strength to tensile strength) , characterized in that the mass percentages of chemical components of the steel plate are C 0.05-0.09; Si 0.2-0.4; Mn 1.3-1.6; Al 0.02-0.04; Nb 0.03-0.08; V 0.03-0.08; Cr 0.1-0.5; Ni 0.1-0.5; Mo 0.1-0.3; Cu 0.2-0.5; Ti 0.01-0.02; P≤0.015; S≤0.003; N≤0.007 , the balance being Fe and inevitable impurities , carbon equivalent is ≤0.43 , cold cracking sensitivity coefficient Pcm is ≤0.20.2. The ultra-heavy steel plate with low cracking sensitivity and low yield ratio according to claim 1 , characterized in that the steel plate has a thickness of 40-70 mm claim 1 , a yield strength of ≥460 MPa claim 1 , a tensile strength of 570-760 MPa claim 1 , a yield ratio of ≤0.80 claim 1 , an elongation rate of ≥17% claim 1 , Charpy impact energy of ≥150 J when it is measured at ¼ thickness and ½ thickness of the steel plates at the temperature of −60° C. claim 1 , a reduction of area in Z direction is ≥35% claim 1 , which can serve at a temperature of −60° C.3. A method for manufacturing the ultra-heavy steel plate with low cracking ...

HIGH-STRENGTH COLD-ROLLED STEEL SHEET AND METHOD OF MANUFACTURING THE SAME

A high-strength cold-rolled steel sheet has a composition and a microstructure. The microstructure comprises: ferrite having an average grain size of 5 um or less and a volume fraction of 3% to 20%, retained austenite having a volume fraction of 5% to 20%, and martensite having a volume fraction of 5% to 20%, the remainder being bainite and/or tempered martensite. The total number of retained austenite with a grain size of 2 μm or less, martensite with a grain size of 2 μm or less, or a mixed phase thereof is 150 or more per 2,000 μmof a thickness cross section parallel to the rolling direction of the steel sheet. 16-. (canceled)8. The high-strength cold-rolled steel sheet according to claim 7 , wherein the composition further contains at least one selected from the group consisting of 0.10% or less V claim 7 , 0.10% or less Nb claim 7 , and 0.10% or less Ti on a mass basis.9. The high-strength cold-rolled steel sheet according to claim 7 , wherein the composition further contains 0.0050% or less B on a mass basis.10. The high-strength cold-rolled steel sheet according to claim 7 , wherein the composition further contains at least one selected from the group consisting of 0.50% or less Cr claim 7 , 0.50% or less Mo claim 7 , 0.50% or less Cu claim 7 , and 0.50% or less Ni on a mass basis.11. The high-strength cold-rolled steel sheet according to claim 7 , wherein the composition further contains at least one selected from the group consisting of 0.0050% or less Ca and 0.0050% or less of a REM on a mass basis. This disclosure relates to high-strength cold-rolled steel sheets and methods of manufacturing the same and particularly relates to a high-strength cold-rolled steel sheet suitable for use in members for structural parts of automobiles and the like and a method of manufacturing the high-strength cold-rolled steel sheet.In recent years, COemissions have been strictly regulated due to growing environmental issues. In the automotive field, improvements in fuel ...

HIGH-YIELD-RATIO, HIGH-STRENGTH COLD ROLLED STEEL SHEET AND PRODUCTION METHOD THEREFOR

A steel sheet includes a microstructure containing a volume fraction of 20% to 55% of ferrite having an average grain size of 7 μm or less, a volume fraction of 5% to 15% of retained austenite, a volume fraction of 0.5% to 7% of martensite having an average grain size of 4 μm or less, and a structure composed of bainite and/or tempered martensite and having an average grain size of 6 μm or less, and a difference in nano-hardness between ferrite and the structure composed of bainite and/or tempered martensite being 3.5 GPa or less and a difference in nano-hardness between the structure composed of bainite and/or tempered martensite and martensite being 2.5 GPa or less. 15.-. (canceled)6. A high-yield-ratio , high-strength cold rolled steel sheet , comprising a composition and a microstructure ,the composition comprising, in terms of percent by mass, C: 0.05% to 0.15%, Si: 0.6% to 2.5%, Mn: 2.2% to 3.5%, P: 0.08% or less, S: 0.010% or less, Al: 0.01% to 0.08%, N: 0.010% or less, Ti: 0.002% to 0.05%, B: 0.0002% to 0.0050%, and the balance being Fe and unavoidable impurities,the microstructure comprising a volume fraction of 20% to 55% of ferrite having an average grain size of 7 μm or less, a volume fraction of 5% to 15% of retained austenite, a volume fraction of 0.5% to 7% of martensite having an average grain size of 4 μm or less, and a structure composed of composed of bainite and/or tempered martensite and having an average grain size of 6 μm or less, anda difference in nano-hardness between the ferrite and the structure composed of composed of bainite and/or tempered martensite being 3.5 GPa or less, anda difference in nano-hardness between the structure composed of composed of bainite and/or tempered martensite and the martensite being 2.5 GPa or less.7. The steel sheet according to claim 6 , wherein the composition further comprises claim 6 , in terms of percent by mass claim 6 , at least one selected from V: 0.10% or less and Nb: 10% or less.8. The steel sheet ...

Micro-alloyed high-strength multi-phase steel containing silicon and having a minimum tensile strength of 750 mpa and improved properties and method for producing a strip from said steel

A high-strength multi-phase steel having minimum tensile strengths of 750 MPa and preferably having a dual-phase microstructure for a cold- or hot-rolled steel strip, in particular for lightweight vehicle construction is disclosed. The high-strength multi-phase steel has improved forming properties and a ratio of yield point to tensile strength of at most 73%. The high-strength multi-phase steel includes in mass %: C≧0.075 to ≦0.105; Si≧0.600 to ≦0.800; Mn≧1.000 to ≦0.700; Cr≧0.100 to ≦0.480; Al≧0.010 to ≦0.060; N 0.0020≦0.0120; S≦0.0030; Nb≧0.005 to ≦0.050; Ti≧0.0050 to ≦0.050; B≧0.0005 to ≦0.0040; Mo≦0.200; Cu≦0.040%; Ni≦0.040% the remainder iron, including typical elements accompanying steel that are not mentioned above, which represent contamination resulting from smelting.

HIGH-IMPACT-TOUGHNESS STEEL RAIL AND PRODUCTION METHOD THEREOF

The invention relates to a high-impact-toughness steel rail and a production method thereof, and belongs to the field of steel rail material production. The present invention is to provide a high-impact-toughness steel rail. The high-impact-toughness steel rail provided in the present invention is a pearlite steel rail with 0.05˜0.09 μm of inter-lamellar spacing and 30˜35 J of ballistic work at normal temperature; the chemical components of the steel rail in weight percentage are: C: 0.71-0.82 wt %, Si: 0.25-0.45 wt %, Mn: 0.75-1.05 wt %, V: 0.03-0.15 wt %, P: ≦0.030 wt %, S: ≦0.035 wt %, Al: ≦0.020 wt %, and Fe and inevitable impurities of the remaining content. The U-type impact toughness of rail head of the steel rail manufactured with the method disclosed in the present invention can be 30 J or more, and the tensile strength is about 1,300 MPa or higher. 1. A high-impact-toughness steel rail , belonging to a pearlite steel rail , with 0.05˜0.09 μm of inter-lamellar spacing and 30˜35 J of ballistic work at normal temperature;the chemical components of the steel rail in weight percentage are: C: 0.71˜0.82 wt %, Si: 0.25˜0.45 wt %, Mn: 0.75˜1.05 wt %, V: 0.03˜0.15 wt %, P: ≦0.030 wt %, S: ≦0.035 wt %, Al: ≦0.040 wt %, and Fe and inevitable impurities of the remaining content.2. The high-impact-toughness steel rail according to claim 1 , wherein the chemical components of the steel rail in weight percentage are: C: 0.71˜0.82 wt % claim 1 , Si: 0.25˜0.45 wt % claim 1 , Mn: 0.75˜1.05 wt % claim 1 , V: 0.03˜0.15 wt % claim 1 , P: ≦0.030 wt % claim 1 , S: ≦0.035 wt % claim 1 , Al: ≦0.020 wt % claim 1 , and Fe and inevitable impurities of the remaining content.3. The high-impact-toughness steel rail according to claim 1 , wherein the chemical components of the steel rail in weight percentage are: C: 0.72˜0.76 wt % claim 1 , Si: 0.35˜0.37 wt % claim 1 , Mn: 0.95˜0.99 wt % claim 1 , V: 0.05˜0.09 wt % claim 1 , P: ≦0.012 wt % claim 1 , S: ≦0.011 wt % claim 1 , Al: ≦0.04 wt ...

Selective Grain Boundary Engineering

A process for grain boundary engineering of an aluminum alloy of AA5XXX series which includes steps of annealing the aluminum alloy at a first temperature of from about 350° C. to about 450° C.; deforming the annealed aluminum alloy to reduce the thickness by from about 2% to about 20% of the original thickness of the aluminum alloy; heat treating the deformed aluminum alloy at a second temperature from about 450° C. to about 550° C., and optionally sensitizing the heat treated alloy in one or more sensitizing steps. Aluminum alloys of the AA5XXX series treated by the process of the present invention are also provided. 1. A process for grain boundary engineering of an aluminum alloy of AA5XXX series , said process comprising steps of:annealing said aluminum alloy at a temperature of from about 350° C. to about 450° C.;deforming said annealed aluminum alloy to reduce the thickness by from about 2% to about 20% of the original thickness of the aluminum alloy; andheat treating said deformed aluminum alloy at a temperature of from about 450° C. to about 550° C.2. The process of claim 1 , wherein said temperature in said annealing step is from about 370° C. to about 430° C. claim 1 , or from about 380° C. to about 420° C.3. The process of claim 1 , wherein said annealing step is performed for a period from about 0.5 to about 3 hours claim 1 , or from about 1 to about 2 hours.4. The process of claim 1 , further comprising the step of cooling the annealed aluminum alloy before the deforming step.5. The process of claim 4 , wherein said cooling step has a cooling rate of from about 10 to about 30° C. per minute claim 4 , or from about 15 to about 25° C. per minute claim 4 , or from about 18 to about 22° C. per minute.6. The process of claim 1 , wherein said deforming step comprises cold rolling.7. The process of claim 6 , wherein said cold rolling reduces the thickness from 3% to 15%.8. The process of claim 6 , wherein said cold rolling reduces the thickness from 5% to 10%. ...

TURBINE ROTOR MATERIAL FOR GEOTHERMAL POWER GENERATION AND METHOD FOR PRODUCING THE SAME

A turbine rotor material for geothermal power generation containing C: 0.20 to 0.30 mass %, Si: 0.01 to 0.2 mass %, Mn: 0.5 to 1.5 mass %, Cr: 2.0 to 3.5 mass %, V: more than 0.15 mass % and 0.35 mass % or less, predetermined amounts of Ni and Mo, and a remainder consisting of Fe and inevitable impurities, the Ni made to be more than 0 and 0.25 mass % or less, the Mo made to be 1.05 to 1.5 mass %. Even a body diameter of 1600 mm or more can thereby be quenched, enabling provision of a turbine rotor material for geothermal power generation less prone to stress corrosion cracking even in a hydrogen sulfide environment and a method for producing the same. 14-. (canceled)5. A turbine rotor material for geothermal power generation , comprising:C: 0.20 to 0.30 mass %;Si: 0.01 to 0.2 mass %;Mn: 0.5 to 1.5 mass %;Cr: 2.0 to 3.5 mass %;V: more than 0.15 mass % and 0.35 mass % or less;predetermined amounts of Ni and Mo; anda remainder consisting of Fe and inevitable impurities, the Ni made to be more than 0 and0.25 mass % or less, the Mo made to be 1.05 to 1.5 mass %.6. The turbine rotor material for geothermal power generation according to claim 5 ,wherein there is no ferrite in a matrix structure and the matrix structure is a bainitic homogeneous microstructure.7. The turbine rotor material for geothermal power generation according to claim 5 ,wherein the turbine rotor material for geothermal power generation is provided with a body having a diameter of at least 1600 mm, room-temperature 0.2% yield strength of 685 MPa or more, room-temperature Charpy impact absorption energy of 20 J or more, and ductility-brittleness transition temperature of 80° C. or lower.8. The turbine rotor material for geothermal power generation according to claim 6 , wherein the turbine rotor material for geothermal power generation is provided with a body having a diameter of at least 1600 mm claim 6 , room-temperature 0.2% yield strength of 685 MPa or more claim 6 , room-temperature Charpy impact ...

STEEL FOR RESISTANCE TO COMPLEX CORROSION FROM HYDROCHLORIC ACID AND SULFURIC ACID, HAVING EXCELLENT WEAR RESISTANCE AND SURFACE QUALITIES, AND METHOD OF MANUFACTURING THE SAME

There are provided a steel sheet for resistance to composite corrosion from sulfuric acid and hydrochloric acid, having excellent wear resistance and surface quality, and a method of manufacturing the same. The steel sheet having excellent surface qualities may be provided by improving resistance to erosion occurring due to coal cinders to increase a lifespan thereof and securing excellent resistance to composite corrosion from sulfuric acid and hydrochloric acid. Wear resistance may be significantly increased by adding P, and in order to solve a problem in that wear resistance is deteriorated due to the addition of P, a component system and a hot rolling process condition may be controlled, thereby forming a corrosion resistant layer having excellent corrosion resistance. 1. A steel sheet for resistance to composite corrosion from sulfuric acid and hydrochloric acid , having excellent wear resistance and surface quality , the steel sheet comprising:carbon (C) of 0.1 weight % or less (except for 0), silicon (Si) of less than 0.1 weight % (except for 0), manganese (Mn) of 0.5 to 1.5 weight %, silicon (S) of 0.02 weight % or less, phosphorous (P) of greater than 0.03 to 0.15 weight %, aluminum (Al) of less than 0.05 weight %, copper (Cu) of 0.1 to 1.0 weight %, nickel (Ni) of 0.1 to 0.4 weight %, cobalt (Co) of 0.03 to 0.1 weight %, antimony (Sb) of 0.05 to 0.15 weight %, remaining iron (Fe), and other inevitably contained impurities; anda single or composite concentration layer formed of one or more selected from a group consisting of copper (Cu), cobalt (Co), nickel (Ni) and antimony (Sb) and formed directly under a surface of the steel sheet to have a thickness of 100 to 300 nm.2. The steel sheet for resistance to composite corrosion of claim 1 , wherein P has a content of 0.051 to 0.15 weight %.3. The steel sheet for resistance to composite corrosion of claim 1 , wherein the steel sheet is represented by the following relational expression claim 1 , where Q has a ...

High-pressure-torsion apparatuses and methods of modifying material properties of workpieces using such apparatuses

A high-pressure-torsion apparatus ( 100 ), comprising a working axis ( 102 ), a first anvil ( 110 ), a second anvil ( 120 ), and an annular body ( 130 ). The annular body ( 130 ) comprises a first total-loss convective chiller ( 140 ), a second total-loss convective chiller ( 150 ), and a heater ( 160 ). Each of the first total-loss convective chiller ( 140 ) and the second total-loss convective chiller ( 150 ) is translatable between the first anvil ( 110 ) and the second anvil ( 120 ) along the working axis ( 102 ), is configured to be thermally convectively coupled with a workpiece ( 190 ), and is configured to selectively cool the workpiece ( 190 ). The heater ( 160 ) is positioned between the first total-loss convective chiller ( 140 ) and the second total-loss convective chiller ( 150 ) along the working axis ( 102 ), is translatable between the first anvil ( 110 ) and the second anvil ( 120 ) along the working axis ( 102 ), and is configured to selectively heat the workpiece ( 190 ).

HIGH-PRESSURE-TORSION APPARATUSES AND METHODS OF MODIFYING MATERIAL PROPERTIES OF WORKPIECES USING SUCH APPARATUSES

A high-pressure-torsion apparatus () comprises a working axis (), a first anvil (), a second anvil (), and an annular body (). The annular body () comprises a a first recirculating convective chiller (), a second recirculating convective chiller (), and a heater (). Each of the first recirculating convective chiller () and the second recirculating convective chiller () is translatable between the first anvil () and the second anvil () along the working axis (), is configured to be thermally convectively coupled with a workpiece (), and is configured to selectively cool the workpiece (). The heater () is positioned between the first recirculating convective chiller () and the second recirculating convective chiller () along the working axis (), is translatable between the first anvil () and the second anvil () along the working axis (), and is configured to selectively heat the workpiece (). 1100. A high-pressure-torsion apparatus () , comprising:{'b': '102', 'a working axis ();'}{'b': '110', 'a first anvil ();'}{'b': 120', '110', '110', '102, 'claim-text': [{'b': 110', '120', '102, 'the first anvil () and the second anvil () are translatable relative to each other along the working axis (), and'}, {'b': 110', '120', '102, 'the first anvil () and the second anvil () are rotatable relative to each other about the working axis (); and'}], 'a second anvil (), facing the first anvil () and spaced apart from the first anvil () along the working axis (), and wherein{'b': '130', 'claim-text': [{'b': '140', 'claim-text': [{'b': 110', '120', '102, 'translatable between the first anvil () and the second anvil () along the working axis ();'}, {'b': '190', 'configured to be thermally convectively coupled with a workpiece (); and'}, {'b': '190', 'configured to selectively cool the workpiece ();'}], 'a first recirculating convective chiller (), which is, {'b': '150', 'claim-text': [{'b': 110', '120', '102, 'translatable between the first anvil () and the second anvil () along the ...

HIGH-PRESSURE-TORSION APPARATUSES AND METHODS OF MODIFYING MATERIAL PROPERTIES OF WORKPIECES USING SUCH APPARATUSES

A high-pressure-torsion apparatus () comprises a working axis (), a first anvil (), a second anvil (), and an annular body (). The annular body () comprises a first conductive chiller (), a second conductive chiller (), and a heater (). Each of the first conductive chiller () and the second conductive chiller () is translatable between the first anvil () and the second anvil () along the working axis (), is configured to be thermally conductively coupled with a workpiece (), and is configured to selectively cool the workpiece (). The heater () is positioned between the first conductive chiller () and the second conductive chiller () along the working axis (), is translatable between the first anvil () and the second anvil () along the working axis (), and is configured to selectively heat the workpiece (). 1100. A high-pressure-torsion apparatus () , comprising:{'b': '102', 'a working axis ();'}{'b': '110', 'a first anvil ();'}{'b': 120', '110', '110', '102, 'claim-text': [{'b': 110', '120', '102, 'the first anvil () and the second anvil () are translatable relative to each other along the working axis (), and'}, {'b': 110', '120', '102, 'the first anvil () and the second anvil () are rotatable relative to each other about the working axis (); and'}], 'a second anvil (), facing the first anvil () and spaced apart from the first anvil () along the working axis (), and wherein{'b': '130', 'claim-text': [{'b': '140', 'claim-text': [{'b': 110', '120', '102, 'translatable between the first anvil () and the second anvil () along the working axis ();'}, {'b': 190', '194', '195', '102, 'configured to be thermally conductively coupled with a workpiece () that has a surface () and a central axis (), collinear with the working axis (); and'}, {'b': '190', 'configured to selectively cool the workpiece ();'}], 'a first conductive chiller (), which is, {'b': '150', 'claim-text': [{'b': 110', '120', '102, 'translatable between the first anvil () and the second anvil () along the ...

MANUFACTURING METHOD FOR VERY HIGH-STRENGTH, COLD-ROLLED, DUAL-PHASE STEEL SHEETS AND SHEETS SO PRODUCED

The present invention provides a cold-rolled and annealed Dual-Phase steel sheet having strength from 980 to 1100 MPa and a breaking elongation greater than 9%. The composition includes the contents being expressed by weight: 0.055%≦C≦0.095%, 2%≦Mn≦2.6%, 0.005%≦Si≦0.35%, S≦0.005%, P≦0.050%, 0.1≦Al≦0.3%, 0.05%≦Mo≦0.25%, 0.2%≦Cr≦0.5%, Cr+2Mo≦0.6%, Ni≦0.1%, 0.010≦Nb≦0.040%, 0.010≦Ti≦0.050%, 0.0005≦B≦0.0025%, and 0.002%≦N≦0.007%. The remainder of the composition includes iron and inevitable impurities resulting from the smelting. A manufacturing method is also provided. 1. A cold-rolled and annealed Dual-Phase steel sheet comprising: [{'br': None, '0.055%≦C≦0.095%'}, {'br': None, '2%≦Mn≦2.6%'}, {'br': None, '0.005%≦Si≦0.35%'}, {'br': None, 'S≦0.005%'}, {'br': None, 'P≦0.050%'}, {'br': None, '0.1≦Al≦0.3%'}, {'br': None, '0.05%≦Mo≦0.25%'}, {'br': None, '0.2%≦Cr≦0.5%'}, {'br': None, 'Cr+2Mo≦0.6%'}, {'br': None, 'Ni≦0.1%'}, {'br': None, '0.010≦Nb≦0.040%'}, {'br': None, '0.010≦Ti≦0.050%'}, {'br': None, '0.0005≦B≦0.0025% and'}, {'br': None, '0.002%≦N≦0.007%,'}, 'a remainder of the composition comprising iron and the inevitable impurities resulting from smelting;, 'a composition comprising, the contents being expressed by weightstrength between 980 and 1100 MPa;a breaking elongation greater than 9%; anda microstructure including a non-recrystallized ferrite fraction less than or equal to 15%.2. The steel sheet as recited in claim 1 , wherein the composition of the steel contains claim 1 , the content being expressed by weight: 0.12%≦Al≦0.25%.3. The steel sheet as recited in claim 1 , wherein the composition of the steel contains claim 1 , the content being expressed by weight: 0.10%≦Si≦0.30%.4. The steel sheet as recited in claim 1 , wherein the composition of the steel contains claim 1 , the content being expressed by weight: 0.15%≦Si≦0.28%.5. The steel sheet as recited in claim 1 , wherein the composition of the steel contains claim 1 , the content being expressed by weight: ...

Additive Manufacturing, Spatial Heat Treating System And Method

An additive manufacturing system including a two-dimensional energy patterning system for imaging a powder bed is disclosed. The two-dimensional energy patterning system may be used to control the rate of cooling experienced by each successive additive layer. Accordingly, the system may be used to heat treat the various additive layers. 1. A method of additive manufacture , the method comprising:distributing a layer of a granular material;directing first radiant energy at a first portion of the layer;amalgamating, by the first radiant energy, all granules of the granular material that correspond to the first portion; andlowering a rate at which heat leaves the first portion after the amalgamating by directing second radiant energy at a second portion of the layer, wherein the second portion is adjacent the first portion and the second radiant energy is insufficient to amalgamate any granules of the granular material that correspond the second portion.2. The method of claim 1 , wherein:the directing the first radiant energy at the first portion occurs for a first period of time; andthe directing the second radiant energy at the second portion occurs for a second period of time.3. The method of claim 2 , wherein the first period of time and the second period of time are equal in length.4. The method of claim 2 , wherein the first period of time and the second period of time begin at the same time.5. The method of claim 2 , wherein the first period of time and the second period of time end at the same time.6. The method of claim 2 , wherein the second period of time extends longer than the first period of time.7. The method of claim 1 , wherein the amalgamating comprises heating claim 1 , by the first radiant energy claim 1 , all granules of the granular material that correspond to the first portion to at least a melting point thereof.8. The method of claim 1 , further comprising generating claim 1 , by a diode array claim 1 , a source radiant energy.9. The method of ...

7000 Series Aluminum Alloy Ladder, Multipurpose Ladder and Method

A ladder and a multipurpose ladder whose rungs and rails are made out of 7000 series aluminum alloy and which has a duty rating of at least 250 lbs. A method for producing a ladder. A method for using a ladder.

MAGNETIC PHASE-TRANSFORMATION MATERIAL

A magnetic phase-transformation material with the formula NiMnCoTiis provided, wherein a+b+c=100, 20 Подробнее

HIGH-STRENGTH HOT-ROLLED STEEL SHEET AND METHOD FOR PRODUCING THE SAME

A steel slab having a composition containing C: more than 0.07% and 0.2% or less, Si: 2.0% or less, Mn: 1.0% to 3.0%, Al: 0.1% or less, Ti: 0.05% to 0.3%, and V: 0.05% to 0.3% on a mass percent basis is heated to 1100° C. or more and is subjected to rough rolling and finish rolling. In the finish rolling, the total rolling reduction of two final passes is 30% or more, and the finish rolling temperature ranges from (Atransformation temperature) to (Atransformation temperature+120° C.). Cooling is started within 2 seconds after the finish rolling. Coiling is performed at an average cooling rate of 40° C./s or more at a coiling temperature in the range of 300° C. to 500° C. The resulting high-strength hot-rolled steel sheet has a microstructure in which a bainite phase constitutes more than 90% by volume, the average lath interval of bainite is 0.45 μm or less, and the ratio of Fe-based carbide precipitated in bainite lath to all Fe-based carbide is 10% or more, has a high tensile strength of 900 MPa or more, and has significantly improved punchability in mass production. 1. A high-strength hot-rolled steel sheet having a composition containing , on a mass percent basis ,C: 0.05% to 0.15%, Si: 1.5% or less,Mn: 1.0% to 2.0%, P: 0.05% or less,S: 0.005% or less, Al: 0.1% or less,N: 0.01% or less, Ti: 0.05% to 0.2%, andthe balance being Fe and incidental impurities,wherein the high-strength hot-rolled steel sheet has a microstructure comprising a bainite of more than 92% by volume, the bainite having an average lath interval of 0.60 μm or less, and Fe-based carbide precipitated in bainite lath grains having a ratio of 10% or more by number to all Fe-based carbide.2. The high-strength hot-rolled steel sheet according to claim 1 , wherein the composition further contains at least one selected from Nb: 0.005% to 0.2% and B: 0.0002% to 0.0030% on a mass percent basis.3. The high-strength hot-rolled steel sheet according to claim 1 , wherein the composition further contains at ...

METHOD FOR INCREASING THE STRAIGHTNESS OF A THIN WIRE

A method for producing a further wire, wherein the method includes, providing a first wire and feeding the first wire through a furnace to obtain the further wire. A further cast of the further wire is larger than a first cast of the first wire.

MICRO-ALLOYED HIGH-STRENGTH MULTI-PHASE STEEL CONTAINING SILICON AND HAVING A MINIMUM TENSILE STRENGTH OF 750 MPA AND IMPROVED PROPERTIES AND METHOD FOR PRODUCING A STRIP FROM SAID STEEL

A high-strength multi-phase steel having minimum tensile strengths of 750 M:Pa and preferably having a dual-phase microstructure for a cold- or hot-rolled steel strip, in particular for lightweight vehicle construction is disclosed. The high-strength multi-phase steel has improved forming properties and a ratio of yield point to tensile strength of at most 73%. The high-strength multi-phase steel includes in mass %: C≥0.075 to ≤0.105; Si≥0.600 to ≤0.800; Mn≥1.000 to ≤0.700; Cr≥0.100 to ≤0.480; Al≥0.010 to ≤0.060; N 0.0020≤0.0120; S≤0.0030; Nb≥0.005 to ≤0.050; Ti≥0.0050 to ≤0.050; B≥0.0005 to ≤0.0040; Mo≤0.200; Cu≤0.040%; Ni≤0.040 % the remainder iron, including typical elements accompanying steel that are not mentioned above, which represent contamination resulting from smelting. 1. A method , comprising:producing a steel strip from of a steel having a composition comprising the elements, in mass %:C≥0.0751 to ≤0.105Si≥0.600 to ≤0.800Mn≥1.000 to ≤1.900Cr≥0.100 to ≤0.700Al≥0.010 to ≤0.060N 0.0020≤0.0120S≤0.0030Nb≥0.005 to ≤0.050Ti≥0.0050 to ≤0.050B≥0.0005 to ≤0.0040Mo≤0.200Cu≤0.040 %Ni≤0.040%remainder iron and steel accompanying elements constituting smelting related impurities,heating the steel strip during a continuous annealing to an annealing temperature in a range of about 700 to 950° C.;cooling the annealed steel strip from the annealing temperature to a first intermediate temperature of about 300 to 500° C. with a cooling rate of between about 15 and 100° C/s; and after the cooling to the intermediate temperature treating the steel strip as set forth under a) or b):a) cooling the steel strip to a second intermediate temperature of about 160 to 250° C. with a cooling rate of between 15 and 100° C./s and after cooling to the second intermediate temperature cooling the steel strip at air to room temperature;b) maintaining the cooling of the steel strip with a cooling rate of between about 15 and 100° C./s from the first intermediate temperature to room ...

GALVANNEALED STEEL SHEET AND METHOD OF MANUFACTURING THE SAME

A galvannealed steel sheet includes: a steel sheet; a coating layer on a surface of the steel sheet; and a mixed layer formed between the steel sheet and the coating layer, in which the mixed layer includes a base iron portion having fine grains having a size of greater than 0 μm and equal to or smaller than 2 μm, a Zn—Fe alloy phase, and oxides containing one or more types of Mn, Si, Al, and Cr, and in the mixed layer, the oxides and the Zn—Fe alloy phase are present in grain boundaries that form the fine grains and the Zn—Fe alloy phase is tangled with the base iron portion.

High strength multi-phase steel, and method for producing a strip from said steel

A high-strength multiphase steel with minimum tensile strengths of 580 MPa, preferably having a dual-phase structure for a cold-rolled or hot-rolled steel strip with improved forming properties, particularly for lightweight vehicle construction contains the elements (contents in mass-%): C 0.075 to ≦0.105; Si 0.600 to ≦0.800; Mn 1.000 to ≦2.250; Cr 0.280 to ≦0.480; Al 0.010 to ≦0.060; P≦0.020; N≦0.0100; S≦0.0150, remainder iron, including typical steel-accompanying elements not mentioned above, which are impurities introduced by smelting, with the condition that the Mn content is preferably ≦1.500% for strip thicknesses up to 1 mm, the Mn content is preferably ≦1.750% for strip thicknesses of 1 to 2 mm, and the Mn content is preferably ≧1.500% for strip thicknesses ≧2 mm

METHOD FOR RESTORING THE STRUCTURE OF A STEEL COMPONENT AFTER HEATING AND STEEL COMPONENT OBTAINED BY THE METHOD

The present disclosure relates to a method for restoring the steel structure of a steel component after heating the steps of heating the steel component to a temperature of at least 1100° C., quenching the steel component to a temperature above the martinsite start temperature (Ms), and maintaining the steel component at that temperature for a holding time sufficient for transformation of all austenite, re-heating the steel component to a temperature of 950 to 1110° C., quenching the steel component to a temperature above the martensite start temperature (Ms), and maintaining the steel component at that temperature for a holding time sufficient for transformation of all austenite, re-heating the steel component to a temperature of above the Actransformation temperature and below 800° C., and maintaining the steel component at that temperature for a holding time sufficient for inititation and completion of spheroidization, and cooling the steel component when the spheroidization is completed, and maintaining a cooling rate of 20° C./h or below during cooling from the Artransformation temperature and until the Artransformation temperature is reached. 1. A method for restoring a steel structure for a steel component after heating characterized in that it comprises the steps of:a) heating a steel component to a temperature of at least 1100° C.,b) quenching the steel component to a temperature of above the martensite start temperature (Ms), and maintaining the steel component at that temperature for a holding time sufficient for transformation of all austenite,c) re-heating the steel component to a temperature of 950 to 1110° C.,d) quenching the steel component to a temperature of above the martensite start temperature (Ms), and maintaining the steel component at that temperature for a holding time sufficient for transformation of all austenite,{'sub': '1', 'e) re-heating the steel component to a temperature of above Actransformation temperature and below 800° C., and ...

APPARATUS FOR THE THERMAL TREATMENT OF METALLIC PRODUCTS

The invention relates to an apparatus () for the thermal treatment of metallic products, which comprises (a) a support and transport plane () for locating and advancing a product to be treated; (b) at least one collector module () comprising (b-) at least one collector (), the collector () being provided with (b-) a perforated plate () on that side of the collector () which is facing the support and transport plane (); (b-) a conduit () connected to said at least one collector () for feeding it with a fluid, and (b-) integrated in said conduit (), at least one stop valve (), in particular an on-off valve, to permit or preclude the flow of said fluid into said at least one collector (). The stop valve () is situated at a distance from the collector () which does not exceed 60 cm, preferably does not exceed 35 cm, and still more preferably does not exceed 10 cm. The perforated plate () is provided with holes () which are arranged in rows () parallel to each other but not in parallel rows with respect to the sides () of said perforated plate. The of an acute angle (). 1. An apparatus for the thermal treatment of metallic products , comprisinga support and transport plane to place and forward a product to be treated; 'a collector including a perforated plate on a side of the collector facing the support and transport plane;', 'a collector module that comprisesa conduit connected to the collector to feed the collector with a fluid, and a stop valve connected to the conduit and configured to permit or preclude the flow of the fluid into the collector; wherein the stop valve is located at a distance from the collector that does not exceed 60 cm, and that the perforated plate includes holes arranged in rows parallel to each other but not in parallel rows with respect to two opposite sides of the perforated plate, and wherein the rows are inclined with respect to the two opposite sides of the plate at an acute angle (β).2. The apparatus for the thermal treatment of metallic ...

Method for repairing break of universal connecting rod of universal coupling

A method for repairing break of a universal connecting rod of a universal coupling includes steps of: cleaning and detecting cracks, providing primary anneal, depositing alloys, providing secondary anneal, manually milling and controlling a quality; wherein depositing the alloys includes forming gradient in an order of a bonding layer, a transition layer, a working layer and a processing layer; wherein the bonding layer: S and P in the depositing area are diluted with an FGM-KM1 material, for removing or reducing the S and P, so as to avoid cold and hot cracks; the transition layer: which is formed by an FGM-KM2 material for improving impact toughness and evacuation stress, and appropriate increasing hardness; the working layer: which is formed by an FGM-KM3 material for improving heat resistance, wear resistance and load capacity; and the processing layer: an FGM-KM4 material is used to reduce surface hardness and improve processing performance. 1. A method for repairing break of a universal connecting rod of a universal coupling , comprising steps of:1) cleaning and detecting cracks, for identifying damage degrees of different parts of the universal connecting rod of the universal coupling; wherein the step 1) specifically comprises steps of:a: cleaning surface greasy dirt, a rust layer, a fatigue layer and irregular cracks, combining colored crack detection and ultrasound crack detection for ensuring base cracks are completely detected and an accurate detection result is obtained; wherein no potential defects are neglected;{'img': {'@id': 'CUSTOM-CHARACTER-00004', '@he': '4.23mm', '@wi': '2.12mm', '@file': 'US20150368733A1-20151224-P00001.TIF', '@alt': 'custom-character', '@img-content': 'character', '@img-format': 'tif'}, 'b: if the cracks exist at a joint of an axle end of the universal connecting rod and a body axle, where a shear stress is most concentrated, eliminating by turning; specifically, defining the crack as a center line, turning a U-shaped groove ...

HIGH-STRENGTH COLD-ROLLED STEEL SHEET HAVING EXCELLENT BENDABILITY

A high strength cold-rolled steel sheet has a component composition containing specific amounts of C, Si, Mn, P, S, N and Al, respectively with a remainder being iron and inevitable impurities. The steel sheet contains 95% or more of martensite in terms of area ratio, and contains 5% or less (inclusive of 0%) of residual austenite and ferrite in terms of a total area ratio. An average size of a carbide is 60 nm or less in terms of an equivalent circle diameter, and a number density of the carbide having the equivalent circle diameter of 25 nm or more is 5.0×10pieces or less per mm. The steel sheet has a yield strength of 1,180 MPa or more and a tensile strength of 1,470 MPa or more. 1. A high strength cold-rolled steel sheet excellent in bendability , having a component composition comprising , by mass %:C: 0.15 to 0.30%;Si: 1.0 to 3.0%;Mn: 0.1 to 5.0%;P: 0.1% or less (exclusive of 0%);S: 0.010% or less (exclusive of 0%);N: 0.01% or less (exclusive of 0%); andAl: 0.001 to 0.10%, with a remainder being iron and inevitable impurities,wherein the high strength cold-rolled steel sheet contains 95% or more of martensite in terms of area ratio, and contains 5% or less (inclusive of 0%) of residual austenite and ferrite in terms of a total area ratio,{'sup': 5', '2, 'an average size of a carbide is 60 nm or less in terms of an equivalent circle diameter, and a number density of the carbide having the equivalent circle diameter of 25 nm or more is 5.0×10pieces or less per mm, and'}the high strength cold-rolled steel sheet has a yield strength of 1,180 MPa or more and a tensile strength of 1,470 MPa or more.2. The high strength cold-rolled steel sheet excellent in bendability according to claim 1 , wherein an average grain size of prior austenite in the martensite is 6 μm or less.3. The high strength cold-rolled steel sheet excellent in bendability according to claim 1 , wherein the component composition further comprises one kind or two or more kinds of:Cu: 0.05 to 1.0%;Ni: ...

FERRITIC STAINLESS STEEL SHEET WHICH IS EXCELLENT IN WORKABILITY AND METHOD OF PRODUCTION OF SAME

Ferritic stainless steel sheet which is excellent in ridging resistance which comprises, by mass %, Cr: 10 to 30%, Sn: 0.005 to 1%, C: 0.001 to 0.1%, N: 0.001 to 0.1%, Si: 0.01 to 3.0%, Mn: 0.01 to 3.0%, P: 0.005 to 0.1%, and S: 0.0001 to 0.01% and has a balance of Fe and unavoidable impurities and which has an X-ray diffraction strength in the {100}<012> orientation from a surface layer to t/4 (“t” is sheet thickness) of 2 or more. 1. A ferritic stainless steel sheet excellent in workability comprising , by mass % , Cr: 10 to 30% , Sn: 0.005 to 1% , C: 0.001 to 0.1% , N: 0.001 to 0.1% , Si: 0.01 to 3.0% , Mn: 0.01 to 3.0% , P: 0.005 to 0.1% , S: 0.0001 to 0.01% and a balance of Fe and unavoidable impurities , wherein an X-ray diffraction strength in the {100}<012> orientation from a surface layer of the steel sheet to t/4 is 2 or more , wherein “t” represents the sheet thickness.2. The ferritic stainless steel sheet excellent in workability according to further comprising claim 1 , by mass % claim 1 , one or more of Ti: 0.005 to 0.5% claim 1 , Nb: 0.005 to 0.5% claim 1 , Zr: 0.005 to 0.5% claim 1 , V: 0.01 to 0.5% claim 1 , Ni: 0.01 to 1% claim 1 , Mo: 0.1 to 3.0% claim 1 , W: 0.1 to 3.0% claim 1 , Cu: 0.1 to 3.0% claim 1 , B: 0.0003 to 0.0100% claim 1 , Al: 0.01 to 1.0% claim 1 , Ca: 0.0001 to 0.003% claim 1 , Mg: 0.0001 to 0.005% claim 1 , Co: 0.001 to 0.5% claim 1 , Sb: 0.005 to 0.3% claim 1 , REM: 0.001 to 0.2% claim 1 , and Ga: 0.0002 to 0.3% or less.3. A method of producing ferritic stainless steel sheet excellent in workability according to claim 1 , the method comprising the steps of: heating a hot rolled steel sheet to 850° C. during annealing the steel sheet; cooling the steel sheet down to 500° C. by a cooling speed of 50° C./sec or less; and cold rolling the steel sheet using rolls of a diameter of 150 mm or less by a reduction rate of 60% or more.4. A method of producing ferritic stainless steel sheet excellent in workability according to claim 2 , the ...

FERRITIC STAINLESS STEEL SHEET HAVING EXCELLENT HEAT RESISTANCE

This ferritic stainless steel sheet contains, in terms of % by mass, 0.02% or less of C, 0.02% or less of N, 0.10% to 0.60% of Si, 0.10% to 0.80% of Mn, 15.0% to 21.0% of Cr, more than 2.00% to 3.50% or less of Cu, 0.30% to 0.80% of Nb, 1.00% to 2.50% of Mo, and 0.0003% to 0.0030% of B, with a remainder being Fe and unavoidable impurities, wherein a maximum particle size of ε-Cu that is present in a structure is 20 nm to 200 nm. 1. A ferritic stainless steel sheet having excellent heat resistance , comprising , in terms of % by mass:C: 0.02% or less;N: 0.02% or less;Si: 0.10% to 0.60%;Mn: 0.10% to 0.80%;Cr: 15.0% to 21.0%;Cu: more than 2.00% to 3.50% or less;Nb: 0.30% to 0.80%;Mo: 1.00% to 2.50%; andB: 0.0003% to 0.0030%,with a remainder being Fe and unavoidable impurities,wherein a maximum particle size of ε-Cu that is present in a structure is 20 nm to 200 nm.2. The ferritic stainless steel sheet having excellent heat resistance according to claim 1 , further comprising claim 1 , in terms of % by mass:one or more selected from W: 2.0% or less, Mg: 0.0050% or less, Ni: 1.0% or less, Co: 1.0% or less, and Ta: 0.50% or less.3. The ferritic stainless steel sheet having excellent heat resistance according to claim 1 , further comprising claim 1 , in terms of % by mass:one or more selected from Al: 1.0% or less, V: 0.50% or less, Sn: 0.5% or less, Sb: 0.5% or less, Ga: 0.1% or less, Zr: 0.30% or less, and REM (rare-earth metal): 0.2% or less.4. A method of manufacturing the ferritic stainless steel sheet having excellent high-temperature strength according to claim 1 , the method comprising:a process of annealing a cold-rolled sheet,wherein a final annealing temperature of the cold-rolled sheet is 1000° C. to 1100° C.,an average cooling rate in a temperature range from an end of a final annealing to 700° C. is 20° C./second or more, andan average cooling rate in a temperature range from 700° C. to 500° C. is 3° C./second to 20° C./second.5. The ferritic stainless steel ...

Thick steel plate for high heat input welding and having great heat-affected area toughness and manufacturing method therefor

A thick steel plate for high heat input welding and having great heat-affected area toughness and a manufacturing method therefor, comprising the steps of smelting, casting, rolling, and cooling. Chemical composition is properly controlled for the steel plate and satisfies 1≤Ti/N≤6 and Mg/Ti>0.017, where effective S content in steel=S−1.3 Mg−0.8 Ca−0.34 REM−0.35 Zr, and effective S content in steel: 0.0003-0.003%; finely dispersed inclusions may be formed in the steel plate, and the amount of composite inclusion MgO+Ti 2 O 3 +MnS in the steel plate is controlled at a proportion greater than or equal to 5%. The tensile strength of a base material so acquired is ≥510 MPa, insofar as welding input energy is 200−400 kJ/cm, the average Charpy impact work of the steel plate at −40 ° C. is 100 J or more, at the same time, the average Charpy aging impact work of the base material of ½ thickness at −40° C. is 46 J or more.

Device for cooling hot steel slabs

High strength multiphase steel and method of making a strip of this steel having a minimum tensile strength of 580 MPa

Die Erfindung betrifft einen hochfesten Mehrphasenstahl mit Mindestzugfestigkeiten von 580 MPa vorzugsweise mit Dualphasengefüge für ein kalt- oder warmgewalztes Stahlband mit verbesserten Umformeigenschaften, insbesondere für den Fahrzeugleichtbau. Der Mehrphasenstahl besteht aus den Elementen (Gehalte in Masse-%): C 0,075 bis ≤ 0,105 Si 0,600 bis ≤ 0,800 Mn 1,000 bis ≤ 2,250 Cr 0,280 bis ≤ 0,480 Al 0,010 bis ≤ 0,060 P ≤ 0,020 N ≤ 0,0100 S ≤ 0,0150 Rest Eisen, einschließlich üblicher stahlbegleitender oben nicht erwähnter Elemente, die erschmelzungsbedingte Verunreinigungen darstellen. The invention relates to a high-strength multiphase steel with minimum tensile strengths of 580 MPa, preferably with dual-phase structure for a cold or hot rolled steel strip with improved forming properties, especially for lightweight vehicle construction. The multiphase steel consists of the elements (contents in mass%): C 0.075 to ≦ 0.105 Si 0.600 to ≦ 0.800 Mn 1.000 to ≦ 2.250 Cr 0.280 to ≦ 0.480 Al 0.010 to ≦ 0.060 P ≦ 0.020 N ≦ 0.0100 S ≦ 0 , 0150 The remainder of iron, including common steel-accompanying elements not mentioned above, which are contaminants due to fusion.

高温鋼材の保温方法

(57)【要約】本公報は電子出願前の出願データであるた め要約のデータは記録されません。

Vorrichtung zum Kuehlen von blank zu erhaltendem Gluehgut

一种具有超高屈强比的吉帕级贝氏体钢及其制造方法

本发明公开了一种具有超高屈强比的吉帕级贝氏体钢，其除了Fe以外还含有质量百分含量如下化学元素：C：0.12～0.24％；Si：0.2～0.5％；Mn：1.3～2.0％；B：0.001～0.004％；Cr、Nb、Ti和Mo中的至少一种，其中Cr≤0.4％，Nb≤0.06％，Ti≤0.1％，Mo≤0.4％。此外本发明还公开了一种用于上述钢材的制造方法和退火工艺，退火工艺包括步骤：(a)在加热段以≤50℃/s的加热速率加热至均热温度Ts：840～900℃(b)在均热段以温度Ts保温5min以下(c)在缓冷段以≤15℃/s的第一冷却速度冷却至(Ts‑80)～(Ts‑140)℃(d)在快冷段以≥(130‑Q)℃/s的第二冷却速度冷却至(Ts‑490)～(Ts‑440)℃，Q＝C×180+Si×10+Mn×30+Ni×50+Cr×15+Mo×15+B×2000(e)在自返温控冷段，以第三冷却速度冷却10～40s，[(Q‑80)/12]≤第三冷却速度≤[(Q‑80)/8](f)在空冷段带钢空冷至室温。

Method for manufacture of steel sheet (versions) and steel sheet

FIELD: manufacture of sheets from superstrong weldable low-alloy steels with excellent ductility at cryogenic temperatures. SUBSTANCE: method involves heating steel slab including iron and specific content of some or all of admixtures of group of admixtures consisting of carbon, nickel, manganese, nitrogen, copper, chromium, molybdenum, silicon, niobium, vanadium, titanium, aluminum and boron; reducing slab for forming of sheet in one or several passes within temperature range providing for recrystallization of austenite; providing finishing rolling of sheet in one or several passes in temperature range below austenite recrystallization temperature and above Ar 3 transition temperature; quenching ready rolled steel sheet to specific quenching stopping temperature; terminating quenching process; cooling by holding sheet for predetermined time at quenching stopping temperature, or by slow cooling of sheet before air cooling, or by merely cooling of sheet in air to ambient temperature. Superstrong weldable low-alloy steel has excellent ductility at cryogenic temperatures in basic sheet and in temperature effect zone during welding. Steel of such structure has tensile strength exceeding 830 MPa and microstructure including fine-crystalline lower bainite, fine-crystalline lamellar martensite, fine-grain bainite or mixture thereof, and up to 10% of retained austenite. Method allows ductile-brittle transition temperature of basic steel in transverse direction and in weldable zone under temperature effect to be reduced to value below -62 0 C. EFFECT: improved quality and improved weldability of sheet steel. 30 cl, 5 dwg, 4 tbl сб 9$ сс ПЧ сэ РОССИЙСКОЕ АГЕНТСТВО ПО ПАТЕНТАМ И ТОВАРНЫМ ЗНАКАМ (19) ВИ” 2 235 792‘ (51) МПК? 13) С2 С 210 8/02 12) ОПИСАНИЕ ИЗОБРЕТЕНИЯ К ПАТЕНТУ РОССИЙСКОЙ ФЕДЕРАЦИИ (21), (22) Заявка: 2001119979/02, 16.12.1999 (24) Дата начала действия патента: 16.12.199911.1-30 (30) Приоритет: 19.12.1998 Ш$ 09/215,773 (43) Дата публикации заявки: 27.05.2003 (46) ...

A kind of high formability galvanizing ultrahigh-strength steel plates and manufacture method thereof

一种高成形性热镀锌超高强度钢板及其制造方法，其化学成分重量百分比为：C 0.15~0.25wt%，Si 1.00~2.00wt%，Mn 1.50~3.00wt%，P≤0.015wt%，S≤0.012wt%，Al 0.03~0.06wt%，N≤0.008wt%，其余为Fe和不可避免杂质；钢板室温组织为铁素体10%~30%+马氏体60~80%+残余奥氏体5~15%；屈服强度600~900MPa，抗拉强度980~1200MPa，延伸率15~22%。本发明钢通过适当的成分设计，采用连续退火生产工艺，不需要添加昂贵合金元素，仅适当提高Si、Mn含量再结合退火和炉内气氛控制工艺实现强度的大幅度挺高，且具有较好的塑性，同时钢板镀锌质量良好，可满足汽车用冷轧热镀锌超高强钢的使用要求。

High-strength cold-rolled steel sheet having excellent bendability

본 발명의 고강도 냉연 강판은, 질량%로, C: 0.15∼0.30%, Si: 1.0∼3.0%, Mn: 0.1∼5.0%, P: 0.1% 이하(0%를 포함하지 않음), S: 0.010% 이하(0%를 포함하지 않음), N: 0.01% 이하(0%를 포함하지 않음), Al: 0.001∼0.10%를 포함하며, 잔부가 철 및 불가피적 불순물로 이루어지는 성분 조성을 갖고, 마르텐사이트가 면적률로 95% 이상 함유되는 한편, 잔류 오스테나이트, 페라이트가, 면적률의 합계로 5% 이하(0%를 포함함)이고, 또한 탄화물의 평균 사이즈가 원 상당 직경으로 60nm 이하임과 더불어, 원 상당 직경으로 25nm 이상의 탄화물의 수밀도가 1mm 2 당 5.0×10 5 개 이하이고, 항복 강도가 1180MPa 이상, 인장 강도가 1470MPa 이상이다.

A kind of magnetic phase transition material

本发明提供一种磁相变材料，其化学式为：Ni a‑m Mn b‑n Co m+n Ti c ；其中，a+b+c＝100,20<a≤90，5≤b<50，5≤c≤30，0≤m≤a，0≤n≤b,0<m+n<a+b,a、b、c、m和n单独或组合表示原子百分比含量。该磁相变材料具有高强韧性、高变形率、强磁性和磁场驱动马氏体相变特性。可以广泛应用于高强高韧驱动器，温度和/或磁性敏感元件，磁制冷器件和设备，磁热泵器件，磁存储器，微型机电器件和系统，热磁发电换能元件等领域。

Process for combined casting and heat treatment

A foamed pattern of a desired part is first formed. The pattern is then dipped into a ceramic slurry and the slurry dried in order to form a shell containing the foamed pattern. A heated bed of a particulate medium is formed around the ceramic shell which causes the pattern to evaporate and form a mold. A molten metal is then introduced into the mold and solidified while being held at an elevated temperature for a period of time to accomplish a desired heat treatment of the metal. With this method, the casting does not have to be subsequently heat treated in a separate operation. It can be removed as an as cast casting, having the desired microstructures.

GCr15 bearing steel with low decarburization depth and preparation method thereof

本发明提供了一种低脱碳层深度的GCr15轴承钢及制备方法，属于金属冶炼加工技术领域，在钢坯表面均匀涂刷两层高温防氧化涂料作为防护层后，送入加热炉内分段加热，可有效阻碍轴承钢在加热炉内与氧化性气体发生反应，减少氧化皮和脱碳层的产生，同时还能降低钢的氧化烧损；涂料以凹凸棒土为主体，性能良好稳定，效果更好；钢坯送入加热炉加热后，通过对加热炉内的残氧量、空气过剩系数、炉压等参数进行控制，能够进一步实现对脱碳层深度的有效控制，而且加热炉可以通过设置目标温度进行自动燃烧控制，使用方便；轧制后将钢坯快速冷却到600℃以下后进行缓慢冷却，此时钢坯的氧化比较缓慢，可有效防止碳的扩散，提高钢坯质量。

Method of making cold-rolled sheets from two-phase steel with very high hardness, and sheets thus produced

FIELD: metallurgy. SUBSTANCE: invention relates to metallurgy, particularly, to production of cold-rolled and annealed sheets from two-phase steel.Said steel contains the following substances, in wt %: 0.055≤C≤0.095, 2≤Mn≤2.6, 0.005≤Si≤0.35, S≤0.005, P≤0.050, 0.1≤Al≤0.3, 0.05≤Mo≤0.2, 0.2≤Cr≤0.5, given Cr+2Mo≤0.6, Ni≤0.1, 0.010≤Nb≤0.040, 0.010≤Ti≤0.050, 0.0005≤B≤0.0025, 0.002≤N≤0.007, iron and unavoidable impurities making the rest. Now, semi-finished product is cast. The latter is heated to 1150°C≤T R ≤1250°C and hot-forged at T PL ≥Ar3. Then, coiling is carried out at 500°C≤T bob ≤570°C. Now, descaling is performed as well as cold rolling with reduction of 30-80%. Cold-rolled semi-finished product is heated at the rate of 1°C/s≤V c ≤5°C/s to annealing temperature T M defined as Ac1+40°C≤T M ≤Ac3-30°C/s whereat said product is cured for 30 s≤t M ≤300 s to produce structure comprising austenite. Thereafter it is cooled down to below Ms at rate V sufficient for conversion of entire amount of austenite in martensite. EFFECT: high forming qualities, steel hardness of 980 to 1100 MPa. 19 cl, 3 dwg, 4 tbl, 1 ex РОССИЙСКАЯ ФЕДЕРАЦИЯ (19) RU (11) 2 470 087 (13) C2 (51) МПК C22C 38/58 (2006.01) C21D 8/02 (2006.01) C23C 2/06 (2006.01) ФЕДЕРАЛЬНАЯ СЛУЖБА ПО ИНТЕЛЛЕКТУАЛЬНОЙ СОБСТВЕННОСТИ (12) ОПИСАНИЕ ИЗОБРЕТЕНИЯ К ПАТЕНТУ (21)(22) Заявка: 2010152214/02, 15.05.2009 (24) Дата начала отсчета срока действия патента: 15.05.2009 2 4 7 0 0 8 7 R U (85) Дата начала рассмотрения заявки PCT на национальной фазе: 21.12.2010 C 2 C 2 (56) Список документов, цитированных в отчете о поиске: ЕР 1548142 А1, 29.06.2005. RU 2152450 C1, 10.07.2000. RU 2190685 C1, 10.10.2002. RU 2151214 C1, 20.06.2000. RU 2321667 C2, 10.04.2008. RU 2312163 C2, 10.12.2007. FR 2790009 A1, 25.08.2000. JP 2000-017385 A, 18.01.2000. (86) Заявка PCT: FR 2009/000574 (15.05.2009) (87) Публикация заявки РСТ: WO 2009/150319 (17.12.2009) Адрес для переписки: 109012, Москва, ул. Ильинка, 5/2, ООО "Союзпатент", О.И.Воль (54) ...

Method for producing grain-oriented electrical steel sheet

Thermomechanical treatment method for preparing rare earth bearing steel

本申请提供了一种制备稀土轴承钢的形变热处理方法，通过采用两相区控轧控冷、缓冷坑缓冷、等温球化退火等措施，可有效控制稀土轴承钢的碳化物网状与带状不高于2.0级，显微组织为细小均匀完全球化且不高于3.0级的珠光体组织，从而提高了稀土轴承钢的组织和碳化物均匀性，为下游用户锻造热处理提供优良基材。

Heat treatment for alloy steel material

Method for manufacturing wire rod of medium carbon capable of omitting softening heat treatment and equipment of the same

본 발명은 선재의 제조방법 및 그 장치에 관한 것이다. The present invention relates to a method for producing a wire rod and an apparatus thereof. 본 발명은 중탄소강 선재의 제조방법에 있어서, The present invention provides a method for producing a medium carbon steel wire, C: 0.30~0.45중량%를 함유하는 빌레트를 950~1000℃로 재가열하는 단계; 상기 재가열된 빌레트의 표면과 중심간 온도 차이가 30℃ 이하가 되도록 하면서 760~810℃까지 냉각한 다음, 마무리압연하는 단계; 상기 마무리압연된 선재를 770~810℃에서 권취하는 단계; 및 400~600℃의 분위기에서 0.01~0.1℃/초의 냉각속도로 상기 권취된 선재를 서냉하는 단계;를 포함하여 이루어진다. C: reheating the billet containing 0.30-0.45 weight% to 950-1000 degreeC; Cooling to 760-810 ° C. while finishing a temperature difference between the surface of the reheated billet and the center to be 30 ° C. or less, and then finishing rolling; Winding the finished rolled wire at 770 ° C. to 810 ° C .; And slowly cooling the wound wire at a cooling rate of 0.01-0.1 ° C./sec in an atmosphere of 400-600 ° C .; 또한, 본 발명은 빌레트를 가열하는 가열로(1)와, 상기 가열로(1)에서 배출되어 냉각된 빌레트를 마무리압연하는 마무리압연기(4), 그리고 상기 마무리압연기(4)에서 배출된 선재를 권취하는 권취기(5)로 이루어진 선재의 제조장치에 있어서, In addition, the present invention is a heating furnace (1) for heating the billet, the finishing mill (4) for finishing rolling the billet discharged from the heating furnace (1), and the wire rod discharged from the finishing mill (4) In the manufacturing apparatus of the wire rod consisting of the winding machine (5) to be wound, 상기 마무리압연기(4) 전단에 빌레트의 내외부 온도편차를 줄일 수 있는 온도제어 패스부(2)가 구비되어 있으며, 상기 권취기(5) 후단에 권취된 선재가 균일한 냉각을 유지하기 위한 서냉로(6)가 구비되는 것을 특징으로 한다. A temperature control path (2) is provided at the front end of the finishing mill (4) to reduce the temperature difference between the inside and outside of the billet, and a slow cooling furnace for maintaining uniform cooling of the wire wound at the rear end of the winder (5). (6) is provided. 본 발명은 종래 비연속적으로 실시하던 추가적인 열처리 공정의 생략이 가능하여 공정단축에 의한 제조비용의 절감, 제조공기의 단축, 스케일발생량 저감 및 재고량 감축 등의 효과를 얻을 수가 있다. The present invention can omit the additional heat treatment step that is conventionally performed discontinuously, and thus, ...

Method for manufacturing hot rolled steel sheet

본 발명은 6~10mm 두께의 열연 강판의 압연 후 런-아웃 테이블에서의 냉각속도를 제어하여 균일한 인장강도를 얻을 수 있도록 한 열간 압연 강판의 제조방법에 관한 것이다. 본 발명은 전체 중량에 대해 니오븀이 0.055~0.065wt%이 첨가된 강 슬라브를 Ar3 변태점이상의 온도에서 6~10mm 두께의 강판으로 사상 압연하고, 사상 압연된 강판을 런-아웃 테이블로 이송시키면서 주수량을 조절하여 냉각속도를 8~12℃/sec로 냉각한 후에 코일 형태로 권취하는 것을 포함하여 이루어진 것이다. 이에 따르면 본 발명은 두께에 따른 석출물 성장효과와 결정립 미세 효과에 따라 강도 편차가 심한 6~10mm 두께의 열연 강판의 제조시 압연 후의 주수량 제어를 통해 냉각속도를 조절함으로써, 균일한 인장강도 범위를 갖는 유용한 효과를 갖는다. 열연 강판, 냉각속도, 인장강도, 두께, 석출물

HIGH-STRENGTH MULTI-PHASE STEEL AND METHOD FOR STRIP MANUFACTURE FROM THIS STEEL WITH MINIMUM TENSILE STRENGTH AT 580 MPa

FIELD: metallurgy. SUBSTANCE: invention relates to the high-strength multi-phase steel with the minimum tensile strength 580 MPa, preferably with two-phase structure, to manufacture the cold-rolled or hot-rolled steel strip with thickness 0.50-4.00 mm with improved moulding properties, used, in particular, for automotive industry with the lightweight structures use. Steel consists of elements, wt %: C from 0.075 to ≤0.105, Si from 0.600 to ≤0.800, Mn from 1.000 to ≤2.250, Cr from 0.280 to ≤0.480, Al from 0.010 to ≤0.060, P ≤0.020, N ≤0.0100, S ≤0.0150, the rest - iron, due to the impurity melting. With the strips thickness up to 1 mm the content of Mn is preferably ≤1.500%, with the strips thickness from 1 mm up to 2 mm, the content of Mn is preferably ≤1.750%, and with the strips thickness ≥2 mm, the Mn content is preferably ≥1.500%. EFFECT: uniform mechanical and technological strips properties and its suitability for the hot-dip galvanizing. 17 cl, 8 dwg, 4 ex РОССИЙСКАЯ ФЕДЕРАЦИЯ (19) RU (11) (13) 2 627 068 C2 (51) МПК C22C 38/38 (2006.01) C22C 38/18 (2006.01) C21D 8/02 (2006.01) C21D 9/46 (2006.01) C23C 2/06 (2006.01) ФЕДЕРАЛЬНАЯ СЛУЖБА ПО ИНТЕЛЛЕКТУАЛЬНОЙ СОБСТВЕННОСТИ (12) ОПИСАНИЕ ИЗОБРЕТЕНИЯ К ПАТЕНТУ (21)(22) Заявка: 2015101783, 24.05.2013 (24) Дата начала отсчета срока действия патента: 24.05.2013 Дата регистрации: (73) Патентообладатель(и): ЗАЛЬЦГИТТЕР ФЛАХШТАЛЬ ГМБХ (DE) Приоритет(ы): (30) Конвенционный приоритет: 22.06.2012 DE 10 2012 013 113.5 (56) Список документов, цитированных в отчете о поиске: DE 10161465 C1, 13.02.2003. RU 2246552 C2, 20.02.2005. RU 2451094 C2, 20.05.2012. RU 2323983 C2, 10.05.2008. JP 11293396 A, 26.10.1999. (45) Опубликовано: 03.08.2017 Бюл. № 22 (85) Дата начала рассмотрения заявки PCT на национальной фазе: 22.01.2015 (86) Заявка PCT: DE 2013/000299 (24.05.2013) (87) Публикация заявки PCT: 2 6 2 7 0 6 8 (43) Дата публикации заявки: 20.08.2016 Бюл. № 23 R U 03.08.2017 (72) Автор(ы): ШУЛЬЦ, Томас (DE), БЕХТОЛЬД, Марион (DE), ...

Method of spheroidizing heat treatment for steel

본 발명은 시멘타이트나 석출물 입자를 단시간에 효과적으로 구상화 처리하는 강의 구상화 열처리 방법에 관한 것으로; 본 발명의 목적은, 관련공정에 있어 열간소성가공 공정과 구상화 열처리 공정 사이에 불림 열처리 공정을 필요로 하지 않기 때문에 전체 공정의 진행이 빨라지게 하는 한편, 상기한 기존의 강의 구상화 열처리 방법에 있어 구상화에 필요한 시간을 줄여주는 동시에 구상화율을 높여주기 위한 것이며; 상기 목적을 달성하기 위해서, 본 발명은, 초기조직을 AC1+{10℃~[(AC3 또는 AC㎝-AC1)/2]}의 오스테나이트화 온도까지 가열하는 단계, 가열된 조직을 상기 AC1+{10℃~[(AC3 또는 AC㎝-AC1)/2]}의 오스테나이트화 온도에서 유지하는 단계, 유지된 조직을 상기 AC1+{10℃~[(AC3 또는 AC㎝-AC1)/2]}의 오스테나이트화 온도에서 Pf-(20~70℃)의 구상화 종료 온도까지 시간당 5~40℃의 속도로 냉각하는 단계, 및 냉각된 조직을 상기 Pf-(20~70℃)의 구상화 종료 온도에서 등온유지 또는 연속서냉하는 단계로 구성되는 것을 특징으로 하는 강의 구상화 열처리 방법을 제공해준다. The present invention relates to a spheroidizing heat treatment method of steel for spheroidizing effectively cementite or precipitate particles in a short time; It is an object of the present invention to speed up the progress of the entire process because it does not require a soaking heat treatment process between the hot firing process and the nodular heat treatment process in the related process, while the spheroidizing heat treatment method of the above-described conventional spheroidizing heat treatment of steel To reduce the time required for the process and increase the visualization rate; In order to achieve the above object, the present invention, the step of heating the initial tissue to the austenitization temperature of AC1 + {10 ° C ~ [(AC3 or ACcm-AC1) / 2]}, the heated tissue is the AC1 + {10 Holding at an austenitization temperature of ° C ~ [(AC3 or ACcm-AC1) / 2]}, retaining the retained tissue as the austenite of AC1 + {10 ° C ~ [(AC3 or ACcm-AC1) / 2]} Cooling at a rate of 5-40 ° C. per hour from nitrification temperature to the spheroidization end temperature of Pf- (20-70 ° C.), and maintaining the isothermally at the spheroidization end temperature of Pf- (20-70 ° C.) Or it provides a spherical heat treatment method of the steel, characterized in that consisting of a continuous slow cooling step.

A kind of residual forging heat normalizing method of steel

一种钢的锻造余热正火方法，是实施在线锻造余热控锻控冷等温正火处理。包括：钢的控锻，即控制钢的锻造温度和锻造变形度，通过奥氏体变形与再结晶导致细化晶粒；钢的控冷，根据金属学和热处理原理；控制钢的各临界温度的冷却速率、冷却均匀性和冷却效率，钢冷却至临界温度等温保持，过冷奥氏体在此温度范围转变完毕，得到细的晶粒组织，等温保持后控冷，即等温保持后控制冷却速率、冷却均匀性和冷却效率及冷却终止温度，获得组织和力学性能达标的正火方法。本发明能节约能源和资源，提高正火处理质量，降低正火处理成本，减轻工人劳动强度，提高劳动生产率，提前工期。

THERMALLY PROCESSED STEEL MATERIAL AND METHOD FOR ITS MANUFACTURE

РОССИЙСКАЯ ФЕДЕРАЦИЯ (19) RU (11) (13) 2015 150 123 A (51) МПК C22C 38/32 (2006.01) C21D 8/02 (2006.01) ФЕДЕРАЛЬНАЯ СЛУЖБА ПО ИНТЕЛЛЕКТУАЛЬНОЙ СОБСТВЕННОСТИ (12) ЗАЯВКА НА ИЗОБРЕТЕНИЕ (21)(22) Заявка: 2015150123, 06.06.2014 (71) Заявитель(и): НИППОН СТИЛ ЭНД СУМИТОМО МЕТАЛ КОРПОРЕЙШН (JP) Приоритет(ы): (30) Конвенционный приоритет: 07.06.2013 JP 2013-120973 (85) Дата начала рассмотрения заявки PCT на национальной фазе: 11.01.2016 R U (43) Дата публикации заявки: 14.07.2017 Бюл. № 20 (72) Автор(ы): ТАБАТА Синитиро (JP), ХИКИДА Казуо (JP), КОДЗИМА Нобусато (JP), МИЗУИ Наомицу (JP) (86) Заявка PCT: (87) Публикация заявки PCT: WO 2014/196645 (11.12.2014) R U (54) ТЕРМИЧЕСКИ ОБРАБОТАННЫЙ СТАЛЬНОЙ МАТЕРИАЛ И СПОСОБ ЕГО ИЗГОТОВЛЕНИЯ (57) Формула изобретения 1. Термически обработанный стальной материал, содержащий: химическую композицию, выраженную в мас.%: C 0,16-0,38 Mn 0,6-1,5 Cr 0,4-2,0 Ti 0,01-0,10 B 0,001-0,010 Si 0,20 или меньше P 0,05 или меньше S 0,05 или меньше N 0,01 или меньше Ni 0-2,0 Cu 0-1,0 Mo 0-1,0 V 0-1,0 Al 0-1,0 Nb 0-1,0 REM 0-0,1 остаток Fe и примеси; и Стр.: 1 A 2 0 1 5 1 5 0 1 2 3 A Адрес для переписки: 129090, Москва, ул. Б. Спасская, 25, стр. 3, ООО "Юридическая фирма Городисский и Партнеры" 2 0 1 5 1 5 0 1 2 3 JP 2014/065151 (06.06.2014) A 2 0 1 5 1 5 0 1 2 3 A R U 2 0 1 5 1 5 0 1 2 3 Стр.: 2 R U структуру, выраженную как: остаточный аустенит: 1,5% объем или меньше; и остаток: мартенсит. 2. Материал по п. 1, содержащий C от 0,16 до 0,25 мас.%. 3. Материал по п. 1 или 2, имеющий механические свойства, выраженные как отношение предела текучести к пределу прочности: 0,70 или больше. 4. Материал по п. 1 или 2, содержащий, в мас.%: Ni 0,1-2,0 Cu 0,1-1,0 Mo 0,1-1,0 V 0,1-1,0 Al 0,01-1,0 Nb 0,01-1,0 REM 0,001-0,1 любое их сочетание. 5. Способ изготовления материала термически обработанной стали, включающий: нагрев стального листа до точки Ac3 или выше; затем охлаждение стального листа до точки Ms при скорости охлаждения, равной критической скорости ...

High-wear-proof blades for pelletiser and method of their sharpening

Изобретение относится к инструментам, в частности к ножам для гранулирования термопластичных полимеров и способу их заточки. Нож выполнен из инструментальной стали для холодной обработки, имеющей твердость менее 65 единиц по шкале С Роквелла. Перед установкой в гранулятор нож подвергают термической обработке, состоящей в нагревании его до температуры от 500 до 700°С в течение более 5 мин и охлаждении со скоростью, равной или менее 15°С/мин. Заточку лезвий осуществляют путем истирания о поверхность пластины экструзионной головки. Усилие на нож при прижиме к поверхности пластины не более 0,5 Н. Одновременно проводят охлаждение посредством циркуляции термостатической текучей среды с периодически изменяющейся скоростью потока. Обеспечивается высокое качество резки и низкая скорость износа ножей. 3 н. и 7 з.п. ф-лы, 4 ил., 2 табл., 6 пр. РОССИЙСКАЯ ФЕДЕРАЦИЯ (19) RU (11) (13) 2 532 206 C2 (51) МПК C21D 9/18 (2006.01) C21D 1/84 (2006.01) B29B 9/06 (2006.01) ФЕДЕРАЛЬНАЯ СЛУЖБА ПО ИНТЕЛЛЕКТУАЛЬНОЙ СОБСТВЕННОСТИ (12) ОПИСАНИЕ (21)(22) Заявка: ИЗОБРЕТЕНИЯ К ПАТЕНТУ 2011120819/02, 29.10.2009 (24) Дата начала отсчета срока действия патента: 29.10.2009 (72) Автор(ы): ФЕЛИСАРИ,Риккардо (IT), КАСАЛИНИ,Алессандро (IT) (73) Патентообладатель(и): Полимери Эуропа С.п.А. (IT) Приоритет(ы): (30) Конвенционный приоритет: (43) Дата публикации заявки: 20.12.2012 Бюл. № 35 R U 07.11.2008 IT MI2008A001970 (45) Опубликовано: 27.10.2014 Бюл. № 30 C1, 15.01.1994. RU 2015181 C1, 30.06.1994. US 6348109 B1, 19.02.2002 (85) Дата начала рассмотрения заявки PCT на национальной фазе: 07.06.2011 (86) Заявка PCT: 2 5 3 2 2 0 6 (56) Список документов, цитированных в отчете о поиске: JP 09-314555 A, 09.12.1997. RU 2005603 (87) Публикация заявки PCT: WO 2010/051943 (14.05.2010) R U 2 5 3 2 2 0 6 Адрес для переписки: 191036, Санкт-Петербург, а/я 24, "НЕВИНПАТ" (54) ВЫСОКОИЗНОСОСТОЙКИЕ ЛЕЗВИЯ ДЛЯ ГРАНУЛЯТОРА И СПОСОБ ИХ ЗАТОЧКИ (57) Реферат: Изобретение относится к инструментам, в или менее 15°С/мин. Заточку ...

Equipment for hot-rolled sheet annealing, hot-rolled sheet annealing method and method for descaling from silicon-containing hot-rolled steel sheet

FIELD: metallurgy. SUBSTANCE: invention relates to metallurgy. Holding zone and cooling zone, at that on the side up to the heating zone and/or on the side before entering the heating zone there is a quick heating device, through which hot-rolled sheet is heated for not less than 50 °C with heating rate of not less than 15 °C/s to improve descaling performance, scale removal can be carried out only by etching, without the need for mechanical removal of scale or heating of steel sheet during etching. Besides, the method for hot-rolled sheet annealing using the above equipment is proposed. EFFECT: improved descaling and improved quality of the sheet surface equipment for annealing the hot-rolled sheet comprises a heating zone. 10 cl, 3 dwg, 2 tbl РОССИЙСКАЯ ФЕДЕРАЦИЯ (19) RU (11) (13) 2 724 265 C1 (51) МПК C21D 9/60 (2006.01) C21D 8/12 (2006.01) C22C 38/00 (2006.01) ФЕДЕРАЛЬНАЯ СЛУЖБА ПО ИНТЕЛЛЕКТУАЛЬНОЙ СОБСТВЕННОСТИ (12) ОПИСАНИЕ ИЗОБРЕТЕНИЯ К ПАТЕНТУ (52) СПК C21D 9/60 (2020.02); C21D 8/12 (2020.02); C22C 38/00 (2020.02) (21)(22) Заявка: 2019115127, 11.10.2017 (24) Дата начала отсчета срока действия патента: Дата регистрации: 22.06.2020 19.10.2016 JP 2016-205194 (56) Список документов, цитированных в отчете о поиске: RU 2532539 C1, 10.11.2014. JP 2012514131 A, 21.06.2012. RU 2112812 C1, 10.06.1998. RU 2591788 C2, 20.07.2016. RU 2414513 C1, 20.03.2011. (45) Опубликовано: 22.06.2020 Бюл. № 18 (85) Дата начала рассмотрения заявки PCT на национальной фазе: 20.05.2019 (86) Заявка PCT: 2 7 2 4 2 6 5 R U (87) Публикация заявки PCT: WO 2018/074295 (26.04.2018) Адрес для переписки: 101000, Москва, ул. Мясницкая, 13, стр. 5, ООО "Союзпатент", С.Б. Фелициной (54) ОБОРУДОВАНИЕ ДЛЯ ОТЖИГА ГОРЯЧЕКАТАНОГО ЛИСТА, СПОСОБ ОТЖИГА ГОРЯЧЕКАТАНОГО ЛИСТА И СПОСОБ УДАЛЕНИЯ ОКАЛИНЫ С КРЕМНИЙСОДЕРЖАЩЕГО ГОРЯЧЕКАТАНОГО СТАЛЬНОГО ЛИСТА (57) Реферат: Изобретение относится к области не менее чем 15°C/с для улучшения металлургии. Для улучшения характеристики характеристики удаления окалины, ...

Ni-base alloy product and manufacturing method thereof

Superhigh-strength, air-hardening, multiphase steel, having excellent process characteristics, and method of producing said steel

FIELD: metallurgy. SUBSTANCE: invention relates to high-strength, air-hardening, multiphase steel used for production of cold-rolled or hot-rolled strips. Steel has the following composition, wt %: C from 0.075 to 0.145, Si from 0.400 to 0.500, Mn from 1.900 to 2.350, Cr from 0.200 to 0.500, Al from 0.005 to 0.060, N from 0.0020 to 0.0120, S 0.0030 or less, Nb from 0.005 up to 0.060, Ti from 0.005 to 0.060, B from 0.0005 to 0.0030, Mo from 0.200 to 0.300, Ca from 0.0005 to 0.0060, Cu 0.050 or less, Ni 0.050 or less, the rest—iron and unavoidable impurities. EFFECT: steel has tensile strength in non-tempered state equal to 950 MPa, required moldability and weldability. 37 cl, 6 dwg, 2 ex РОССИЙСКАЯ ФЕДЕРАЦИЯ (19) RU (11) (13) 2 721 767 C2 (51) МПК C22C 38/38 (2006.01) C21D 8/02 (2006.01) C21D 9/46 (2006.01) ФЕДЕРАЛЬНАЯ СЛУЖБА ПО ИНТЕЛЛЕКТУАЛЬНОЙ СОБСТВЕННОСТИ (12) ОПИСАНИЕ ИЗОБРЕТЕНИЯ К ПАТЕНТУ (52) СПК C22C 38/38 (2020.02); C21D 8/02 (2020.02); C21D 9/46 (2020.02) (21)(22) Заявка: 2017120860, 06.11.2015 (24) Дата начала отсчета срока действия патента: Дата регистрации: (73) Патентообладатель(и): ЗАЛЬЦГИТТЕР ФЛАХШТАЛЬ ГМБХ (DE) 22.05.2020 18.11.2014 DE 10 2014 017 274.0 (43) Дата публикации заявки: 19.12.2018 Бюл. № 35 (56) Список документов, цитированных в отчете о поиске: EP 2426230 A1, 07.03.2012. RU 2321668 C2, 10.04.2008. RU 2507297 C1, 20.02.2014. WO 2012100762 A1, 02.08.2012. (45) Опубликовано: 22.05.2020 Бюл. № 15 (85) Дата начала рассмотрения заявки PCT на национальной фазе: 19.06.2017 2 7 2 1 7 6 7 Приоритет(ы): (30) Конвенционный приоритет: R U 06.11.2015 (72) Автор(ы): ШУЛЬЦ, Томас (DE), ШЁТЛЕР, Йоахим (DE), КЛЮГЕ, Саша (DE) DE 2015/100474 (06.11.2015) C 2 C 2 (86) Заявка PCT: (87) Публикация заявки PCT: R U 2 7 2 1 7 6 7 WO 2016/078644 (26.05.2016) Адрес для переписки: 109012, Москва, ул. Ильинка, 5/2, ООО "Союзпатент" (54) СВЕРХВЫСОКОПРОЧНАЯ, ЗАКАЛИВАЮЩАЯСЯ НА ВОЗДУХЕ, МНОГОФАЗНАЯ СТАЛЬ, ОБЛАДАЮЩАЯ ОТЛИЧНЫМИ ТЕХНОЛОГИЧЕСКИМИ ХАРАКТЕРИСТИКАМИ, И СПОСОБ ...

Method and device for production of moulded products

FIELD: process engineering. SUBSTANCE: invention relates to metallurgy. Melt is filled in the mould. Said mould is partially withdrawn from hardened cast. Hardened cast is placed on cooling chamber bed while mantle is arranged at said bed to make cooling chamber surround said hardened cast. EFFECT: ruled out heat impact and/or cracking. 15 cl, 6 dwg, 1 tbl, 2 ex РОССИЙСКАЯ ФЕДЕРАЦИЯ (19) RU (11) (51) МПК B22D 30/00 (13) 2 516 417 C2 (2006.01) ФЕДЕРАЛЬНАЯ СЛУЖБА ПО ИНТЕЛЛЕКТУАЛЬНОЙ СОБСТВЕННОСТИ (12) ОПИСАНИЕ (21)(22) Заявка: ИЗОБРЕТЕНИЯ К ПАТЕНТУ 2010114162/02, 09.09.2008 (24) Дата начала отсчета срока действия патента: 09.09.2008 (72) Автор(ы): ПЕДЗУТТИ,Джеймс,Вернон (AU), О'ЛИРИ,Юан (AU) 10.09.2007 AU 2007904899 (43) Дата публикации заявки: 20.10.2011 Бюл. № 29 R U (73) Патентообладатель(и): УИЭР МИНЕРАЛЗ ОСТРЕЙЛИА ЛТД (AU) Приоритет(ы): (30) Конвенционный приоритет: (45) Опубликовано: 20.05.2014 Бюл. № 14 А, 07.05.1982. US 6199618 B1, 13.03.2001. JP 07-195163 A, 01.08.1995 (85) Дата начала рассмотрения заявки PCT на национальной фазе: 12.04.2010 (86) Заявка PCT: 2 5 1 6 4 1 7 (56) Список документов, цитированных в отчете о поиске: GB 1600405 A, 14.10.1981. SU 925546 2 5 1 6 4 1 7 R U (87) Публикация заявки PCT: C 2 C 2 AU 2008/001335 (09.09.2008) WO 2009/033211 (19.03.2009) Адрес для переписки: 109012, Москва, ул. Ильинка, 5/2, ООО "Союзпатент" (54) СПОСОБ И УСТРОЙСТВО ДЛЯ ИЗГОТОВЛЕНИЯ ОТЛИВКИ (57) Реферат: Изобретение относится к литейному полностью окружает отвердевшую отливку. производству. Расплавленный материал заливают Обеспечивается теплообмен между отвердевшей в литейную форму. С полученной отвердевшей отливкой, полный контроль скорости охлаждения отливки частично удаляют литейную форму. отливки для снижения возможности теплового Отвердевшую отливку располагают на основании удара и/или растрескивания отливки. 2 н. и 13 з.п. охлаждающей камеры и устанавливают кожух на ф-лы, 6 ил., 1 табл., 2 пр. основание так, что охлаждающая камера Стр.: 1 RUSSIAN ...

Hot rolling on-line mobile heat preservation heat treatment process

一种热轧在线移动保温热处理工艺，板坯经加热、轧制、层冷、卷取至热卷状态，热卷卸卷打捆完毕后在30min内对热卷加装在线移动保温装置，对热卷开始进行热处理，并同时在线运至热卷保温处理区域；热处理时间1～48h后，采用空冷方式冷却后将钢卷送入库；其中，卷取温度控制在250～750℃之间。本发明热轧在线移动保温热处理工艺有效结合热卷卷取工艺温度，第一时间对热卷进行高效保温热处理，保温处理的热卷随保温装置在线移动，确保实现差异化的热处理工艺需求，不仅可以有效改善产品性能，且一次投资低，满足高节奏的大生产需求，节约能源。

High-strength hot-dip galvanized steel sheet with high ductility and excellent formability

연성 및 성형성이 우수한 고강도 용융아연도금강판이 제공된다. 본 발명의 용융아연도금강판은, 중량%로, 탄소(C): 0.06~0.16%, 실리콘(Si): 0.8% 이하(0% 제외), 망간(Mn): 2.1~2.7%, 몰리브덴(Mo): 0.4% 이하(0% 제외), 크로뮴(Cr): 1% 이하(0% 제외), 인(P): 0.1% 이하(0% 제외), 황(S): 0.02% 이하, 알루미늄(sol.Al): 1% 이하(0% 제외), 타이타늄(Ti): 0.001~0.04%, 나이오븀(Nb): 0.001~0.04%, 질소(N): 0.01% 이하(0% 제외), 붕소(B): 0.01% 이하, 안티몬(Sb): 0.05% 이하, 잔부 Fe 및 기타 불가피한 불순물을 포함하고, 소지강판 두께 1/4t 지점의 기지조직 내 소강 성분 중 C, Si, Al, Mn, Cr, Mo 및 B의 성분이 하기 관계식 1은 만족하고, 소지강판의 미세조직이, 면적%로, 베이나이트 및 템퍼드 마르텐사이트의 합: 70% 이상, 페라이트: 10% 이하, 잔부 프레시 마르텐사이트와 잔류오스테나이트로 구성되며, 상기 잔류오스테나이트 분율이 면적%로 5% 이하이다.

Advanced high strength zinc plated steel sheet having excellent surface quality and spot weldability and manufacturing method thereof

본 발명의 한 가지 측면에 따르면, 표면품질과 점 용접성이 우수한 고강도 용융아연도금 강판 및 그 제조방법이 제공될 수 있다.

PERLITE RAIL OF HIGH ABRASION RESISTANCE AND METHOD OF MANUFACTURING THE SAME

본 발명은 중하중 철도의 급격하게 휘어진 구역이 레일에 요구되는 내마모성과 내손상성을 개선하는 것을 목적으로 0.85초과 1.20%까지의 C, 0.10에서 1.00%의 Si, 0.40에서 1.50%의 Mn, 그리고 필요하다면 Cr, Mo, V, Nb,Co, 그리고 B으로 구성되는 군으로부터 선택되는 적어도 하나의 종으로 이루어지고 열간 압연의 고온을 유지하거나 또는 열처리의 목적으로 고온까지 가열된 강 레일에 관한 것으로 본 발명은 양호한 내마모성과 양호한 내손상성을 가지는 펄라이트 강 게일을 제공하고, 상기 강 레일의 헤드부가 1에서 10°C/초의 속도로 오스테나이트 구역 온도로부터 700에서 500°C의 냉각 정지 온도까지 가속 가열하여서 상기 헤드부의 겨도가 20mm 깊이의 범위내에서는 적어도 Hv320이 되는 상기의 것의 제조방법을 제공한다.

SUPERHIGH-STRENGTH Hardening airborne, MULTI-PHASE STEEL WITH EXCELLENT TECHNOLOGICAL CHARACTERISTICS, AND METHOD FOR PRODUCING INDICATED STEEL

РОССИЙСКАЯ ФЕДЕРАЦИЯ (19) RU (11) (13) 2017 120 860 A (51) МПК C22C 38/02 (2006.01) ФЕДЕРАЛЬНАЯ СЛУЖБА ПО ИНТЕЛЛЕКТУАЛЬНОЙ СОБСТВЕННОСТИ (12) ЗАЯВКА НА ИЗОБРЕТЕНИЕ (21)(22) Заявка: 2017120860, 06.11.2015 (71) Заявитель(и): ЗАЛЬЦГИТТЕР ФЛАХШТАЛЬ ГМБХ (DE) Приоритет(ы): (30) Конвенционный приоритет: 18.11.2014 DE 10 2014 017 274.0 35 R U (43) Дата публикации заявки: 19.12.2018 Бюл. № (72) Автор(ы): ШУЛЬЦ Томас (DE), ШЁТЛЕР Йоахим (DE), КЛЮГЕ Саша (DE) (85) Дата начала рассмотрения заявки PCT на национальной фазе: 19.06.2017 DE 2015/100474 (06.11.2015) (87) Публикация заявки PCT: WO 2016/078644 (26.05.2016) R U (54) СВЕРХВЫСОКОПРОЧНАЯ ЗАКАЛИВАЮЩАЯСЯ НА ВОЗДУХЕ, МНОГОФАЗНАЯ СТАЛЬ, ОБЛАДАЮЩАЯ ОТЛИЧНЫМИ ТЕХНОЛОГИЧЕСКИМИ ХАРАКТЕРИСТИКАМИ, И СПОСОБ ПОЛУЧЕНИЯ УКАЗАННОЙ СТАЛИ (57) Формула изобретения 1. Сверхвысокопрочная, закаливаемая на воздухе, многофазная сталь с минимальным пределом прочности на разрыв в незакаленном на воздухе состоянии, равном 950 МПа, с отличными технологическими характеристиками, включающая элементы (содержание в % по массе): C от ≥ 0,075 до ≤ 0,115 Si от ≥ 0,400 до ≤ 0,500 Mn от ≥ 1,900 до ≤ 2,350 Cr от ≥ 0,200 до ≤ 0,500 Al от ≥ 0,005 до ≤ 0,060 N от ≥ 0,0020 до ≤ 0,0120 S ≤ 0,0030 Nb от ≥ 0,005 до ≤ 0,060 Ti от ≥ 0,005 до ≤ 0,060 B от ≥ 0,0005 до ≤ 0,0030 Mo от ≥ 0,200 до ≤ 0,300 Ca от ≥ 0,0005 до ≤ 0,0060 Cu ≤ 0,050 Ni ≤ 0,050, Стр.: 1 A 2 0 1 7 1 2 0 8 6 0 A Адрес для переписки: 109012, Москва, ул. Ильинка, 5/2, ООО "Союзпатент" 2 0 1 7 1 2 0 8 6 0 (86) Заявка PCT: A 2 0 1 7 1 2 0 8 6 0 A R U 2 0 1 7 1 2 0 8 6 0 Стр.: 2 R U причем остальное приходится на железо и неизбежные примеси, в которой в соответствии с возможным наиболее широким технологическим интервалом во время непрерывного отжига горячей полосы и холодной полосы, изготовленной из этой стали, суммарное содержание (Mn + Si + Cr) установлено в зависимости от толщины полученной полосы следующим образом: вплоть до 1,00 мм: сумма (Mn + Si + Cr) ≥ 2,800 и ≤ 3,000%, свыше 1,00 до 2,00 мм: ...

HIGH-RESISTANT BLADES FOR GRANULATORS AND THE METHOD OF THEIR GRINDING

1. Ножи, выполненные из инструментальной стали для холодной обработки, имеющей твердость менее 65 единиц по шкале С Роквелла, для применения в грануляторах для термопластичных полимеров, которые перед установкой в грануляторы подвергают термической обработке, причем такая термическая обработка состоит в нагревании ножей до температуры от 500 до 700°С в течение более 5 мин, а затем постепенном охлаждении.2. Ножи по п.1, где время нагревания составляет более 20 мин.3. Ножи по п.1, охлаждение которых осуществляют со скоростью, равной или менее 15°С/мин.4. Ножи по п.1, характеризующиеся тем, что нижний угол наклона между лезвием и поверхностью пластины экструзионной головки составляет от 2 до 45°.5. Ножи по п.1, выполненные из ледебуритной инструментальной стали.6. Ножи по любому из предшествующих пунктов, в которых ледебуритная сталь включает хром, молибден и ванадий.7. Ножи по п.6, в которых сталь включает 3-12% ванадия, 4-12% хрома и 1-5% молибдена.8. Способ заточки ножей по любому из пп.1-7, который включает установку ножей в оправку гранулятора, приведение их во вращение, прижим их к поверхности пластины экструзионной головки с усилием более 0,5 Н на нож и одновременное проведение стадии охлаждения посредством циркуляции термостатической жидкости, где скорость потока такой термостатической жидкости периодически изменяют.9. Способ по п.8, в котором текучие среды, находящиеся в емкости гранулятора, являются как газообразными, так и жидкими, и где объемная доля газа составляет более 0,6 и менее 1. РОССИЙСКАЯ ФЕДЕРАЦИЯ (19) RU (11) 2011 120 819 (13) A (51) МПК C21D 1/84 (2006.01) ФЕДЕРАЛЬНАЯ СЛУЖБА ПО ИНТЕЛЛЕКТУАЛЬНОЙ СОБСТВЕННОСТИ (12) ЗАЯВКА НА ИЗОБРЕТЕНИЕ (21)(22) Заявка: 2011120819/02, 29.10.2009 (71) Заявитель(и): Полимери Эуропа С.п.А. (IT) Приоритет(ы): (30) Конвенционный приоритет: 07.11.2008 IT MI2008A001970 (85) Дата начала рассмотрения заявки PCT на национальной фазе: 07.06.2011 (87) Публикация заявки РСТ: WO 2010/051943 (14.05.2010) R U (54) ...

Patent RU2017120860A3

ВУ"? 2017120860” АЗ Дата публикации: 26.07.2019 Форма № 18 ИЗПМ-2011 Федеральная служба по интеллектуальной собственности Федеральное государственное бюджетное учреждение 5 «Федеральный институт промышленной собственности» (ФИПС) ОТЧЕТ О ПОИСКЕ 1. . ИДЕНТИФИКАЦИЯ ЗАЯВКИ Регистрационный номер Дата подачи 2017120860/02(036117) 06.11.2015 РСТ/ОЕ2015/1004774 06.11.2015 Приоритет установлен по дате: [ ] подачи заявки [ ] поступления дополнительных материалов от к ранее поданной заявке № [ ] приоритета по первоначальной заявке № из которой данная заявка выделена [ ] подачи первоначальной заявки № из которой данная заявка выделена [ ] подачи ранее поданной заявки № [Х] подачи первой(ых) заявки(ок) в государстве-участнике Парижской конвенции (31) Номер первой(ых) заявки(ок) (32) Дата подачи первой(ых) заявки(ок) (33) Код страны 1. 10 2014 017 274.0 18.11.2014 РЕ Название изобретения (полезной модели): [Х] - как заявлено; [ ] - уточненное (см. Примечания) СВЕРХВЫСОКОПРОЧНАЯ ЗАКАЛИВАЮЩАЯСЯ НА ВОЗДУХЕ, МНОГОФАЗНАЯ СТАЛЬ, ОБЛАДАЮЩАЯ ОТЛИЧНЫМИ ТЕХНОЛОГИЧЕСКИМИ ХАРАКТЕРИСТИКАМИ, И СПОСОБ ПОЛУЧЕНИЯ УКАЗАННОЙ СТАЛИ Заявитель: ЗАЛЬЦГИТТЕР ФЛАХШТАЛЬ ГМБХ, ОЕ 2. ЕДИНСТВО ИЗОБРЕТЕНИЯ [Х] соблюдено [ ] не соблюдено. Пояснения: см. Примечания 3. ФОРМУЛА ИЗОБРЕТЕНИЯ: [ ] приняты во внимание все пункты (см. Примечания) [Х] приняты во внимание следующие пункты: 1-22 [ ] принята во внимание измененная формула изобретения (см. Примечания) 4. КЛАССИФИКАЦИЯ ОБЪЕКТА ИЗОБРЕТЕНИЯ (ПОЛЕЗНОЙ МОДЕЛИ) (Указываются индексы МПК и индикатор текущей версии) С22С 35/38 (2006.01) С21О 8/02 (2006.01) С21О 9/46 (2006.01) 5. ОБЛАСТЬ ПОИСКА 5.1 Проверенный минимум документации РСТ (указывается индексами МПК) С22С38/00-С22С38/60, С21108/00, С21108/02, С21109/00, С2109/46 5.2 Другая проверенная документация в той мере, в какой она включена в поисковые подборки: 5.3 Электронные базы данных, использованные при поиске (название базы, и если, возможно, поисковые термины): Езрасепеь, ]-Р]а\ Ра, РАТЕМТЗСОРЕ, Раеагсв, ...

rail manufacturing method

빌렛이 레일 형상으로 열간 압연되고 레일이 대기 온도로 냉각되는 레일 제조 방법이 제공된다. 레일의 푸트부는 표면 온도가 800℃ 내지 400℃ 사이인 적어도 냉각 기간동안 레일의 직립성을 향상시키도록 기계적으로 구속될 수 있다. 후속 냉각 공정에서, 적어도 레일 푸트의 표면 온도가 400℃ 내지 250℃이면서, 레일은 직립 상태로 유지되고, 절연 또는 가속화된 냉각을 사용하지 않고 자연스럽게 냉각된다. There is provided a rail manufacturing method wherein the billet is hot rolled into a rail shape and the rail is cooled to ambient temperature. The foot portion of the rail may be mechanically constrained to improve the upstanding of the rail for at least a cooling period at which the surface temperature is between 800 ° C. and 400 ° C. FIG. In a subsequent cooling process, the rails remain upright and naturally cool without the use of insulated or accelerated cooling while at least the surface temperature of the rail foot is 400 ° C to 250 ° C.

QP High-Strength Hot Rolling QP Steel and Method of Manufacturing the Same

본 발명은 700MPa 수준 고강도 열간 압연 Q&P 강 및 이의 제조 방법이며, 상기 강은 다음과 같이 중량%의 화학 조성물을 가진다: C: 0.15%~0.40%; Si: 1.0%~2.0%; Mn: 1.5%~3.0%; P: 0.015% 이하; S: 0.005% 이하; Al: 0.3%~1.0%; N: 0.006% 이하; Ti: 0.005%~0.015%, 및 Fe 및 피할 수 없는 불순물인 나머지; 700Mpa 이상의 항복 강도, 1300Mpa 이상의 인장 강도 및 10% 초과의 신장률을 가진다. 조성물에 대한 합리적인 설계에 의하고 일반적인 C-Mn 강의 조성물을 기초로, 본 발명은 Si의 함유량을 증가시켜 시멘타이트의 침전을 제한하며, 미세-Ti 처리를 실행하여 오스테나이트 과립을 정제하고, Al의 함유량을 증가시켜 공기 냉각 공정 동안 오스테나이트 변형 동력을 빠르게 하고; 동시에, 열간 압연 공정과 단계를 둔 냉각 공정을 결합하여 초석 페라이트와 마르텐사이트와 잔류 오스테나이트의 구조를 얻으며 합금 원소의 비용을 실질적으로 감소시킨다. The present invention is a 700 MPa high strength hot rolled Q & P steel and a method of making the same, wherein the steel has a weight percent chemical composition as follows: C: 0.15% to 0.40%; Si: 1.0% to 2.0%; Mn: 1.5% to 3.0%; P: 0.015% or less; S: 0.005% or less; Al: 0.3% to 1.0%; N: 0.006% or less; Ti: 0.005% to 0.015%, and the balance being Fe and inevitable impurities; A yield strength of 700 Mpa or more, a tensile strength of 1300 Mpa or more, and an elongation of 10% or more. Based on a reasonable design of the composition and based on the composition of a general C-Mn steel, the present invention increases the Si content to limit precipitation of the cementite, performs micro-Ti treatment to purify the austenite granules, To increase the austenite strain power during the air cooling process; At the same time, the hot rolling process and the stepwise cooling process are combined to obtain the structure of pro-eutectoid ferrite, martensite and retained austenite, and substantially reduce the cost of the alloying element.

Hot rolled coated steel sheet having high strength, high formability, excellent bake hardenability and method of manufacturing the same

본 발명은 고강도, 고성형성, 우수한 소부경화성을 갖는 열연도금강판 및 그 제조방법에 관한 것이다. 본 발명의 일 실시형태는 중량%로, C: 0.05~0.14%, Si: 0.1~1.0%, Mn: 1.0~2.0%, P: 0.001~0.05%, S: 0.001~0.01%, Al: 0.01~0.1%, Cr: 0.005~1.0%, Ti: 0.005~0.13%, Nb: 0.005~0.03%, N: 0.001~0.01%, 잔부 Fe 및 기타 불가피한 불순물을 포함하고, 페라이트 및 베이나이트 혼합조직을 주상으로 포함하고, 잔부 조직으로서 마르텐사이트, 오스테나이트 및 도상 마르텐사이트(MA)로 이루어지는 그룹으로부터 선택된 1종 이상을 포함하며, 상기 페라이트 및 베이나이트의 분율은 95~99면적%이고, 하기 관계식 1을 만족하는 고강도, 고성형성, 우수한 소부경화성을 갖는 열연도금강판 및 그 제조방법을 제공한다. [관계식 1] FCO {110}<112> + FCO {112}<111> ≥ 10 (단, FCO {110}<112> 와 FCO {112}<111> 는 각각 {110}<112> 및 {112}<111> 결정방위를 갖는 조직의 면적 분율을 의미함.) The present invention relates to a hot-rolled steel sheet having high strength, high formability, and excellent sintering property and a method for manufacturing the same. In one embodiment of the present invention, by weight, C: 0.05 to 0.14%, Si: 0.1 to 1.0%, Mn: 1.0 to 2.0%, P: 0.001 to 0.05%, S: 0.001 to 0.01%, Al: 0.01 to 0.1%, Cr: 0.005 ~ 1.0%, Ti: 0.005 ~ 0.13%, Nb: 0.005 ~ 0.03%, N: 0.001 ~ 0.01%, the balance contains Fe and other unavoidable impurities, and the ferrite and bainite mixed structure is mainly used. Included, as a residual structure, at least one selected from the group consisting of martensite, austenite and island martensite (MA), the fraction of ferrite and bainite is 95 to 99 area%, satisfying the following relational expression 1 It provides a hot-rolled steel sheet having a high strength, high formability, excellent seizure hardening properties and a method for manufacturing the same. [Relationship 1] FCO {110} <112> + FCO {112} <111> ≥ 10 (However, FCO {110} <112> and FCO {112} <111> refer to the area fraction of tissues with crystal orientations of {110} <112> and {112} <111>, respectively.)

Heating and cooling methods of non-alloyed steel and apparatus

본 발명은 비조질강의 가열·냉각방법 및 그 장치에 관한 것으로, 특히 비조질강재를 가열로(15)에서 1150∼1300℃ 범위로 가열한 후 열간단조하여 단조재(3)를 가공하는 단계와; 열간단조를 거친 상기 단조재(3)를 콘베어벨트(1)에 의해 냉각실(10)에 도달할 때 1000℃이하로 제어하는 단계와; 상기 냉각실(10)을 통과하는 단조재(3)의 온도구배를 지정온도구배대비 30%이내의 오차를 유지하도록 냉각속도를 제어하는 것을 특징으로 하는 비조질강의 가열 및 냉각방법에 관한 것이며, 또한 출구에 온도센서(16)가 설치되면서 상기 온도센서(16)에서 단조재(3)의 온도를 측정하여 중앙연산시스템(20)에 전달하는 가열로(15)와; 입구보다 출구가 더 넓도록 형성되면서 상부에 냉각부(17)가 설치되고, 상기 중앙연산시스템(20)에 연결되는 다수의 온도센서(9,12,4)가 내장되는 냉각실(10)로 구성되는 것을 특징으로 하는 비조질강 가열 및 냉각장치에 관한 것이다.

High strength hot rolled steel sheet and method for producing same

本发明所涉及的高强度热轧钢板具有如下组成：以质量％计含有C：0.05％～0.18％、Si：1.0％以下、Mn：1.0％～3.5％、P：0.04％以下、S：0.006％以下、Al：0.10％以下、N：0.008％以下、Ti：0.05％～0.20％、V：大于0.1％且为0.3％以下，其余部分由Fe和不可避免的杂质构成；且具有如下组织：将以面积率计大于85％的贝氏体相作为主相，将铁素体相、马氏体相及残留奥氏体相中的1种或2种以上作为第2相，以面积率合计含有0％以上且小于15％的该第2相，上述贝氏体相的板条的平均板条间隔为400nm以下，且上述板条的平均长轴长度为5.0μm以下；拉伸强度TS为980MPa以上。

Production method of heavy rail steel for guard rail

本发明一种护轮轨用重轨钢的生产方法，在LF精炼操作时加入渣料造二元碱度3.0～5.0的高碱度白渣进行精炼；待钢水硫含量≤0.012wt%时，加入调渣剂进行调渣处理，控制炉渣碱度为1.5～2.0；加入钛铁使钢水中钛含量控制在0.015wt%～0.025wt%；之后软吹出站上钢；铸坯缓冷步骤采用夹钳下线入缓冷坑缓冷处理，铸坯入坑温度不低于700℃，出坑温度不高于150℃，提供铸坯中氢扩散的良好热力学条件。本发明省去了现有技术中RH或VD精炼步骤，简化了护轮轨用重轨钢的生产工艺流程，降低了生产成本；使铸坯内部各类夹杂物有效控制在≤2.0级，有效降低铸坯内部中心偏析和疏松缺陷，完全满足护轮轨质量要求。

Method of fabricating rails

FIELD: metallurgy. SUBSTANCE: invention refers to metallurgy, particularly to fabricating of rails. To reduce a value of distortion of a rail after cooling a stock is subject to hot rolling to shape it as a rail with a high temperature, then cooling is carried out to the ambient temperature; at that the rail is vertically held; when the temperature of the head of the rail reaches 400°C to 250°C, the rail is naturally cooled avoiding isolation and accelerated cooling within the mentioned range of temperatures; at that vertical distortion of the rail is prevented by means of weight of the rail itself. During cooling part of the rail foot is mechanically maintained within the surface temperature from 800°C to 400°C. EFFECT: development of such method of fabricating rail that prevents vertical rail distortion. 7 cl, 2 ex, 3 tbl, 1 dwg ÐÎÑÑÈÉÑÊÀß ÔÅÄÅÐÀÖÈß RU (19) (11) 2 336 336 (13) C2 (51) ÌÏÊ C21D 9/06 (2006.01) ÔÅÄÅÐÀËÜÍÀß ÑËÓÆÁÀ ÏÎ ÈÍÒÅËËÅÊÒÓÀËÜÍÎÉ ÑÎÁÑÒÂÅÍÍÎÑÒÈ, ÏÀÒÅÍÒÀÌ È ÒÎÂÀÐÍÛÌ ÇÍÀÊÀÌ (12) ÎÏÈÑÀÍÈÅ ÈÇÎÁÐÅÒÅÍÈß Ê ÏÀÒÅÍÒÓ (21), (22) Çà âêà: 2006125717/02, 07.01.2005 (24) Äàòà íà÷àëà îòñ÷åòà ñðîêà äåéñòâè ïàòåíòà: 07.01.2005 (30) Êîíâåíöèîííûé ïðèîðèòåò: 09.01.2004 JP 2004-004358 (73) Ïàòåíòîîáëàäàòåëü(è): ÍÈÏÏÎÍ ÑÒÈË ÊÎÐÏÎÐÅÉØÍ (JP) (43) Äàòà ïóáëèêàöèè çà âêè: 27.01.2008 R U (72) Àâòîð(û): ÎÍÎÄÅÐÀ Íîðèàêè (JP), ÑÀÒÎÕ Òàêó (JP), ÓÅÄÀ Ìàñàõàðó (JP), ÔÓÄÇÈÒÀ Êàçóî (JP), ÊÎÁÀßÑÈ Àêèðà (JP) (45) Îïóáëèêîâàíî: 20.10.2008 Áþë. ¹ 29 2 3 3 6 3 3 6 (56) Ñïèñîê äîêóìåíòîâ, öèòèðîâàííûõ â îò÷åòå î ïîèñêå: JP 59031824 À, 21.02.1984. JP 55002768 A, 10.01.1980. US 3276924 A, 04.10.1966. RU 2101369 C1, 10.01.1998. RU 2128718 C1, 20.10.1998. (85) Äàòà ïåðåâîäà çà âêè PCT íà íàöèîíàëüíóþ ôàçó: 17.07.2006 2 3 3 6 3 3 6 R U (87) Ïóáëèêàöè PCT: WO 2005/066377 (21.07.2005) C 2 C 2 (86) Çà âêà PCT: JP 2005/000427 (07.01.2005) Àäðåñ äë ïåðåïèñêè: 129090, Ìîñêâà, óë. Á. Ñïàññêà , 25, ñòð.3, ÎÎÎ "Þðèäè÷åñêà ôèðìà Ãîðîäèññêèé è Ïàðòíåðû", ïàò.ïîâ. Þ.Ä.Êóçíåöîâó, ðåã.¹ 595 (54) ÑÏÎÑÎÁ ...

Cooling with prevention of oxidation

Galvanized steel plate for hot pressing and method for production of hot-pressed molded article

FIELD: metallurgy. SUBSTANCE: invention relates to galvanized steel sheet for hot pressing used in automotive industry. Zinc-plated steel sheet contains a zinc-plated layer and the main steel sheet. In the region from the boundary between the galvanized layer and the main steel sheet on the side of the main steel sheet at the boundaries and inside the crystalline grains there is an internal oxide containing at least such oxidising elements as Si, Mn and Cr. Main steel sheet has the composition containing the following, wt. %: C: from 0.10 to 0.5, Si: from 0.50 to 2.5, Mn: from 1.0 to 3, Cr: from 0 to 1.0, iron and unavoidable impurities - the rest. Composition of the main steel sheet satisfies the following expression: (2×[Si]/28.1 + [Mn]/54.9 + 1.5×[Cr]/52.0)≥0.05, where [Si], [Mn] and [Cr] are content of Si, Mn and Cr, wt. %, in the main steel sheet, respectively. EFFECT: provides for suppression of cracks formation during pressing due to liquid metal embrittlement. 8 cl, 3 dwg, 4 tbl, 3 ex РОССИЙСКАЯ ФЕДЕРАЦИЯ (19) RU (11) (13) 2 693 226 C1 (51) МПК C22C 38/18 (2006.01) C22C 38/04 (2006.01) B21D 22/20 (2006.01) C23C 2/06 (2006.01) ФЕДЕРАЛЬНАЯ СЛУЖБА ПО ИНТЕЛЛЕКТУАЛЬНОЙ СОБСТВЕННОСТИ (12) ОПИСАНИЕ ИЗОБРЕТЕНИЯ К ПАТЕНТУ (52) СПК C22C 38/18 (2019.02); C22C 38/04 (2019.02); B21D 22/20 (2019.02); C23C 2/06 (2019.02) (21)(22) Заявка: 2018115970, 29.09.2016 (24) Дата начала отсчета срока действия патента: (73) Патентообладатель(и): КАБУСИКИ КАЙСЯ КОБЕ СЕЙКО СЕ (КОБЕ СТИЛ, ЛТД.) (JP) Дата регистрации: 01.07.2019 (56) Список документов, цитированных в отчете о поиске: US 2012/0267012 A1, 25.10.2012. RU 02.10.2015 JP 2015-197226 2464338 C2, 20.10.2012. JP 2014-159624 A, 04.09.2014. JP 2014-224311 A, 04.12.2014. WO 2014199923 A1, 18.12.2014. (45) Опубликовано: 01.07.2019 Бюл. № 19 (85) Дата начала рассмотрения заявки PCT на национальной фазе: 03.05.2018 (86) Заявка PCT: 2 6 9 3 2 2 6 R U (87) Публикация заявки PCT: WO 2017/057570 (06.04.2017) Адрес для переписки: 129090, ...

Installation for heat treatment of metal products

FIELD: heat treatment of metal products. SUBSTANCE: invention relates to an installation (10) for heat treatment of metal products. The installation contains a) a bearing and transport surface (24) for placing and advancing the workpiece, b) at least one module (12) collectors containing b-1) at least one collector (14, 16), and the collector (14 ) is equipped with a perforated plate (22), b-2) pipeline (20) connected to the specified at least one collector (14) for supplying fluid to it, and b-3) at least one shut-off pipeline fittings (18). The shut-off pipeline fittings (18) are located at a distance from the manifold (14) not exceeding 60 cm, preferably not exceeding 35 cm and even more preferably not exceeding 10 cm. The perforated plate (22) has holes arranged in rows (38), parallel to each other, but not parallel to the sides (22a, 22b) of the perforated plate. Rows (38) run at an acute angle (β) with respect to two opposite sides (22a) of the plate (22). EFFECT: invention ensures uniform processing of the product and simplifies the maintenance of the installation. 10 cl, 2 dwg РОССИЙСКАЯ ФЕДЕРАЦИЯ (19) RU (11) (13) 2 744 838 C1 (51) МПК B21B 45/02 (2006.01) ФЕДЕРАЛЬНАЯ СЛУЖБА ПО ИНТЕЛЛЕКТУАЛЬНОЙ СОБСТВЕННОСТИ (12) ОПИСАНИЕ ИЗОБРЕТЕНИЯ К ПАТЕНТУ (52) СПК B21B 45/02 (2021.01) (21)(22) Заявка: 2020123107, 19.12.2018 (24) Дата начала отсчета срока действия патента: Дата регистрации: (73) Патентообладатель(и): ДАНИЭЛИ & К. ОФФИЧИНЕ МЕККАНИКЕ С.П.А. (IT) 16.03.2021 (56) Список документов, цитированных в отчете о поиске: WO 03084686 A1, 16.10.2003. EP 1938911 A1, 02.07.2008. DE 19843038 B4, 12.10.2006. RU 2570712 C1, 10.12.2015. SU 1425220 A1, 23.09.1988. 20.12.2017 IT 102017000147399 (45) Опубликовано: 16.03.2021 Бюл. № 8 (85) Дата начала рассмотрения заявки PCT на национальной фазе: 20.07.2020 (86) Заявка PCT: 2 7 4 4 8 3 8 R U (87) Публикация заявки PCT: WO 2019/123295 (27.06.2019) Адрес для переписки: 105082, Москва, Спартаковский пер., 2, стр. 1, секция 1, ...