The present invention relates to a high-strength steel sheet having excellent formability and impact resistance, and a method for manufacturing a high-strength steel sheet having excellent formability and impact resistance. Background technology [0002] In recent years, automobiles have high strength in order to reduce the weight of the vehicle body, improve fuel efficiency, reduce carbon dioxide emissions, and absorb collision energy in the event of a collision to ensure the protection and safety of passengers. Steel plates are often used. [0003] However, in general, when the strength of a steel sheet is increased, the formability (ductility, hole expandability, etc.) decreases and it becomes difficult to process into a complicated shape. Therefore, the formability (ductility, hole expandability, etc.) and resistance It is not easy to achieve both strength that can ensure impact resistance, and various techniques have been proposed so far. [0004] For example, in Patent Document 1, in a high-strength steel plate of 780 MPa class or higher, the steel plate structure has a space ratio of ferrite: 5 to 50%, retained austenite: 3% or less, and balance: martensite (average aspect ratio: 1). 5. and above), techniques for improving the strength-elongation balance and the strength-elongation flange balance are disclosed. [0005] In Patent Document 2, a composite structure composed of ferrite having an average crystal grain size of 10 μm or less, martensite of 20% by volume or more, and other second phase is formed in a high-strength hot-dip galvanized steel sheet, and has corrosion resistance and resistance. Techniques for improving secondary process brittleness are disclosed. [0006] Patent Documents 3 and 8 disclose a technique for ensuring high elongation even at high strength by using the metal structure of a steel sheet as a composite structure of ferrite (soft structure) and bainite (hard structure). [0007] Patent Document 4 describes in high-strength steel sheets that the space factor is 5 to 30% for ferrite and 50 to 95% for martensite, the average grain size of ferrite is 3 μm or less in diameter equivalent to a circle, and the average grain of martensite. A technique for forming a composite structure having a diameter equivalent to a circle and having a diameter of 6 μm or less to improve elongation and stretch ferrite properties is disclosed. [0008] In Patent Document 5, precipitation-enhanced ferrite precipitated by controlling the precipitation distribution mainly by the precipitation phenomenon (interphase interfacial precipitation) caused by grain boundary diffusion at the phase interface during the transformation from austenite to ferrite is used as the main phase. , A technique for achieving both strength and elongation is disclosed. [0009] Patent Document 6 discloses a technique in which a steel sheet structure has a ferrite single-phase structure and ferrite is reinforced with fine carbides to achieve both strength and elongation. In Patent Document 7, in a high-strength thin steel plate, the austenite grains having a required C concentration at the interface between the ferrite phase, the bainite phase, and the martensite phase and the austenite grains are set to 50% or more, and the elongation and hole expandability are improved. The technology to secure is disclosed. [0010] In recent years, attempts have been made to use high-strength steel of 590 MPa or more in order to significantly reduce the weight of automobiles and improve impact resistance. There is a demand for high-strength steel of 590 MPa or more, which is excellent in ductility, hole widening property, etc.). Prior art literature Patent documents [0011] Patent Document 1: Japanese Unexamined Patent Publication No. 2004-238679 Patent Document 2: Japanese Unexamined Patent Publication No. 2004-323958 Patent Document 3: Japanese Unexamined Patent Publication No. 2006-274318 Patent Document 4: Japanese Unexamined Patent Publication No. 2008-297609 Patent Document 5: Japanese Unexamined Patent Publication No. 2011-225491 Patent Document 6: Japanese Unexamined Patent Publication No. 2012-026032 Patent Document 7: Japanese Unexamined Patent Publication No. 2011-195956 Patent Document 8: Japanese Unexamined Patent Publication No. 2013-181208 Outline of the invention Problems to be solved by the invention [0012] INDUSTRIAL APPLICABILITY The present invention considers that a high-strength steel sheet having a maximum tensile strength (TS) of 590 MPa or more, which realizes weight reduction of an automobile and ensuring impact resistance, is required to have improved formability, and has a TS of 590 MPa or more. For high-strength steels (including galvanized steel sheets, galvanized steel sheets, alloyed galvanized steel sheets, and alloyed zinc alloy plated steel sheets), the problem is to improve formability, and high-strength steel sheets that solve the problems. Another object of the present invention is to provide a method for manufacturing a high-strength steel sheet having excellent formability and impact resistance. Means to solve problems [0013] The present inventors have diligently researched a method for solving the above problems. As a result, if the microstructure of the material steel sheet (heat-treated steel sheet) is formed into a lath structure containing a predetermined carbide and the required heat treatment is applied, the heat-treated steel sheet has high strength and impact resistance and is formable. We have found that it is possible to form an excellent microstructure. [0014] The present invention has been made based on the above findings, and the gist thereof is as follows. [0015] [1] Ingredient composition is mass%, C: 0.080 to 0.500%, Si: 2.50% or less, Mn: 0.50 to 5.00%, P: 0.100% or less, S: 0.0100% or less, Al: 0.001 to 2.000%, N: 0.0150% or less, O: 0.0050% or less, Remaining part: In a steel sheet consisting of Fe and unavoidable impurities and satisfying the following formula (1). The microstructure in the region from 1/8 t (t: plate thickness) to 3/8 t (t: plate thickness) from the surface of the steel plate is by volume%. Needle-shaped ferrite: 20% or more, Island-like hard structure consisting of one or more of martensite, tempered martensite, and retained austenite: 20% or more Including Residual austenite: 2% or more, 25% or less, Bulk ferrite: 20% or less, Pearlite and / or cementite: 5% or less in total Limited to In the island-shaped hard structure, the average aspect ratio of the hard region having a circle equivalent diameter of 1.5 μm or more is 2.0 or more, and the average aspect ratio of the hard region having a circle equivalent diameter of less than 1.5 μm is less than 2.0. And The average number density per unit area of ​​the hard region having a circle equivalent diameter of less than 1.5 μm (hereinafter, also simply referred to as “number density”) is 1.0 × 10 10 pieces · m-2 or more, and 3 pieces. In the above field of view, when the number densities of island-shaped hard structures are obtained in an area of ​​5.0 × 10 -10 m 2 or more, the ratio of the maximum number density to the minimum number density is 2.5 or less. A high-strength steel plate with excellent formability and impact resistance. [Si] +0.35 [Mn] +0.15 [Al] +2.80 [Cr] +0.84 [Mo] +0.50 [Nb] +0.30 [Ti] ≧ 1.00 ・ ・ ・ (1) [Element]: Mass% of element [0016] [2] The composition of the components is further increased by mass%. Ti: 0.300% or less, Nb: 0.100% or less, V: 1.00% or less Including one or more of A high-strength steel plate having excellent formability and impact resistance according to the present invention. [0017] [3] The composition of the components is further increased by mass%. Cr: 2.00% or less, Ni: 2.00% or less, Cu: 2.00% or less, Mo: 1.00% or less, W: 1.00% or less, B: 0.0100% or less Including one or more of A high-strength steel plate having excellent formability and impact resistance according to the present invention. [0018] [4] The composition of the components is further increased by mass%. Sn: 1.00% or less, Sb: 0.200% or less Including one or two of A high-strength steel plate having excellent formability and impact resistance according to the present invention. [0019] [5] The component composition further contains, in mass%, one or more of Ca, Ce, Mg, Zr, La, Hf, and REM in a total of 0.0100% or less. A high-strength steel plate having excellent formability and impact resistance according to the present invention. [0020] [6] The high-strength steel plate of the present invention having excellent formability and impact resistance, characterized by having a zinc-plated layer or a zinc alloy-plated layer on one side or both sides of the high-strength steel plate. [0021] [7] A high-strength steel plate having excellent formability and impact resistance of the present invention, wherein the zinc plating layer or the zinc alloy plating layer is an alloyed plating layer. [0022] [8] After heating the slab containing the component of the present invention to 1080 ° C. or higher and 1300 ° C. or lower, the hot rolling conditions in the temperature range from the maximum heating temperature to 1000 ° C. satisfy the formula (A), and further rolling. A hot rolling process in which hot rolling is performed with a completion temperature in the section of 975 ° C to 850 ° C, and The cooling conditions from the completion of hot rolling to 600 ° C satisfy the following formula (2) representing the total degree of transformation progress in each temperature range obtained by dividing the temperature from the rolling completion temperature to 600 ° C into 15 equal parts. , The cooling step in which the temperature history calculated every 20 ° C. after reaching 600 ° C. until the intermediate heat treatment described later is started satisfies the following formula (3). A cold rolling process that performs cold rolling with a rolling reduction of 80% or less, It is heated from (Ac3-30) ° C. to (Ac3 + 100) ° C. with an average heating rate of 30 ° C./sec or more in the temperature range of 650 ° C. to (Ac3-40) ° C., and from the heating temperature (maximum heating temperature-). 10) An intermediate heat treatment step in which the residence time in the temperature range of ° C. is limited to 100 seconds or less, and then, when cooling from the heating temperature, the average cooling rate in the temperature range of 750 ° C. to 450 ° C. is set to 30 ° C./sec or more. And, to the steel plate for heat treatment obtained by carrying out The temperature history from (Ac1 + 25) ° C. to Ac3 points is within the range that satisfies the following formula (B) from 450 ° C. to 650 ° C., and then the temperature history from 650 ° C. to 750 ° C. is within the range that satisfies the following formula (C). Heat and Keep at the heating temperature for 150 seconds or less, When cooling from the heat holding temperature, set the average cooling rate in the temperature range of 700 ° C to 550 ° C to 10 ° C / sec or more, and cool to the temperature range of 550 ° C to 300 ° C. The residence time in the temperature range of 550 ° C to 300 ° C is set to 1000 seconds or less. Further, the present heat treatment step in which the residence condition in the temperature range of 550 ° C to 300 ° C satisfies the following formula (4) is carried out. The method for producing a high-strength steel sheet having excellent formability and impact resistance according to the present invention. [0023] [Number 1] n: Number of rolling passes up to 1000 ° C after removal from the heating furnace hi: Finishing plate thickness after i-pass [mm] Ti: Rolling temperature of the i-pass [° C] ti: Elapsed time from rolling the i-pass to the i + 1-pass [seconds] A = 9.11 × 10 7, B = 2.72 × 10 4: Constant [0024] [Number 2] T (n): residence time in the nth temperature range [seconds] Element symbol: mass% of element Tf: Hot rolling completion temperature [° C] [0025] [Number 3] T n: average steel sheet temperature from the first calculation time to the nth calculation time [° C] T n: Effective total time [time] for carbide growth at the time of the nth calculation Δt n: Elapsed time from the n-1st calculation time to the nth calculation time [time] C: Parameters related to the growth rate of carbides (element symbol: mass% of element) [0026] [Number 4] However, each chemical composition represents the addition amount [mass%]. F: constant, 2.57 t n: Elapsed time from (440 + 10n) ° C to (450 + 10n) ° C [seconds] K: Value in the middle of equation (3) [0027] [Number 5] M: Constant 5.47 x 10 10 N: Value on the left side of equation (B) P: 0.38Si + 0.64Cr + 0.34Mo However, each chemical composition represents the addition amount [mass%]. Q: 2.43 × 10 4 t n: Elapsed time from (640 + 10n) ° C to (650 + 10n) ° C [seconds] [0028] [Number 6] T (n): Average temperature of the steel sheet in the nth time zone when the residence time is divided into 10 equal parts. Bs point (° C) = 611-33 [Mn] -17 [Cr] -17 [Ni] -21 [Mo] -11 [Si] +30 [Al] + (24 [Cr] +15 [Mo] +5500 [B] +240 [Nb]) / (8 [C]) [Element]: Mass% of element When Bs